JP2011516624A - Microporous membrane, battery separator and battery - Google Patents

Abstract

  A microporous polymer membrane having excellent properties for use as a battery separator is provided. The membrane is produced by stretching and then heat setting the microporous polymer membrane at least in the upstream and downstream stages, wherein the temperature of the upstream stage is at least 15 ° C. lower than the temperature of the downstream stage.

Description

  The present invention relates to a microporous membrane having a standard deviation of permeability that penetrates a thin film in the transverse direction (“TD”) of 15 seconds or less, a puncture strength of 3500 mN or more, and a thickness of 20 μm. It relates to a manufacturing method. The microporous membrane can be used as a battery separator. Microporous membranes also have good heat shrinkage properties and compression resistance. The present invention also relates to a battery separator comprising a microporous membrane, a battery using the battery separator, and a method for producing a microporous membrane for battery use such as charge source and sink. About.

Microporous membranes are primary batteries, lithium ion secondary batteries, lithium-polymer secondary batteries, nickel-hydrogen secondary batteries, nickel-cadmium secondary batteries, nickel-zinc secondary batteries, silver-zinc secondary batteries, etc. It is useful as a separator for secondary batteries. When a microporous membrane is used as a battery separator, particularly in a lithium ion battery, the performance of this membrane significantly affects battery properties, productivity, and safety. That is, the microporous membrane must have suitable permeability, mechanical properties, thermal stability, dimensional stability, shutdown properties, and meltdown properties. Such batteries have a relatively low shutdown temperature and a relatively high melt-down temperature to show improved battery safety, especially when the battery is exposed to high temperatures under operating conditions. Must be. High separator permeability is preferred for high capacity batteries. Separators with high mechanical strength are preferred for improved battery assembly and manufacturing. A uniform and highly permeable distribution across the separator surface is an important physical property. The permeability uniformity of a microporous membrane is characterized by the distribution of air permeability values at two or more points along a line parallel to TD. A relatively high air permeability is characterized by a relatively small standard deviation of the measured air permeability value. Air permeability is often expressed in terms of a “Gurley” value equal to the number of seconds required to pass 100 cm ³ of air through a 1.0 inch 2 material at standard pressure. The Gurley value is conventionally expressed as the number of seconds per 100 cm ³ or the number of seconds (where “100 cm ³ ” is understood). If the air permeability is relatively uniform, for example having approximately the same value at different points along the transverse direction TD, the film trimming required to produce a film with appropriate permeability specifications is more Reduce. This results in less waste and increases the yield of the thin film production line.

Optimization of material composition, stretching conditions, heat treatment conditions, etc. has been proposed to improve the properties of microporous membranes used as battery separators. For example, JP 6-240036A discloses a microporous membrane having improved pore diameter and sharp pore diameter distribution. This membrane is made from a polyethylene resin containing 1% or more by volume of ultra high molecular weight polyethylene having a weight average molecular weight (“Mw”) of 7 × 10 ⁵ or more. This polyethylene resin has a molecular weight distribution (weight average molecular weight / number average molecular weight) of 10 to 300, the microporous membrane has a porosity of 35 to 90%, an average permeation pore diameter of 0.05 to 2 μm, 0 It has a breaking strength (15 mm width) of 2 kg or more and a pore diameter distribution (maximum pore diameter / average permeation pore diameter) of 1.5 or less. This microporous membrane is formed by extruding a molten mixture of the above-mentioned polyethylene resin and film-forming solvent through a die, by cooling from the above-mentioned polyethylene resin crystal dispersion temperature (Tcd) to a melting temperature + 10 ° C., The step of stretching the obtained gel-like sheet, the step of removing the film-forming solvent from this gel-like sheet, the area of the obtained membrane expanded at a temperature of the aforementioned polyethylene melting temperature of −10 ° C. or less, and 1.5 It is manufactured by a process of redrawing up to 3 times and a process of heat-setting in a single step at a temperature between the crystal dispersion temperature and the melting point of the polyethylene resin.

  WO 1999/48959 discloses a microporous polyolefin membrane not only having a uniform pore surface with locally biased permeability, but also having suitable strength and permeability. The membrane is made from a polyolefin resin, for example, a high density polyethylene having a weight average molecular weight Mw of 50,000 or more and less than 5,000,000 and a molecular weight distribution of 1 or more and less than 30 and having a thickness of 20 to 100 nm. Having a network structure with fine gaps formed of uniformly dispersed micro-fibrils having an average microfibril size of 10 to 400 nm and an average fiber distance of 40 to 400 nm. This microporous membrane is cooled through a die through a process of extruding a molten mixture of the polyolefin resin and the film-forming solvent as described above, a melting point temperature of the polyolefin resin of −50 ° C., or a temperature higher or lower than this melting point temperature. The step of stretching the gel-like sheet obtained in this manner, the step of removing the film-forming solvent from the gel-like sheet, the melting point temperature of the polyolefin resin −50 ° C., or a temperature higher or lower than the melting point temperature of the sheet 1.1. It is manufactured by a step of redrawing up to 5 times and a step of heat setting in a single stage at a temperature between the crystal dispersion temperature and the melting point of the polyolefin resin.

WO 2000/20492 discloses an improved permeable microporous polyolefin membrane characterized by fine polyethylene fibers having a weight average molecular weight Mw of 5 × 10 ⁵ or more. The composition includes polyethylene. This microporous polyolefin membrane has an average pore diameter of 0.05 to 5 μm and a ratio of lamellae at an angle θ of 80 to 100 ° with respect to the membrane surface in a longitudinal and transverse cross section of 40% or more. The polyethylene composition comprises 1 to 69% by weight, ultrahigh molecular weight polyethylene having a weight average molecular weight Mw of 7 × 10 ⁵ or more, 1 to 98% high density polyethylene by weight, and 1 to 30% low density polyethylene. . This microporous membrane is formed by extruding a melt blend of the polyethylene composition and a film-forming solvent through a die, stretching a gel-like sheet obtained by cooling, and the crystal dispersion temperature or melting point +30 of the aforementioned polyethylene or composition. Manufactured by single stage heat setting at a temperature of 0 C and removal of the film forming solvent.

  WO 2002/072248 discloses a microporous membrane having improved permeability, particle blocking properties, and strength. This membrane is produced using a polyethylene resin having a weight average molecular weight Mw of less than 380,000. This membrane has a porosity of 50 to 95% and an average pore diameter of 0.01 to 1 μm. This microporous membrane has a three-dimensional network skeleton formed by microfibrils having an average diameter of 0.2 to 1 μm connected to each other throughout the microporous membrane, and has an average of 0.1 μm or more and less than 3 μm It has a gap defined by a skeleton having a diameter. This microporous membrane is obtained by extruding a melt blend of the polyethylene resin and the film-forming solvent through a die and removing the film-forming solvent from the gel-like sheet obtained by cooling, and at 2 to 140 ° C. at a temperature of 20 to 140 ° C. The film is stretched 4 times, and the stretched film is obtained by performing a single-stage heat setting at a temperature of 80 ° C. to 140 °.

  WO 2005/113657 discloses a microporous polyolefin membrane having suitable shutdown properties, meltdown properties, two-dimensional stability, and high temperature resistance. The membrane has (a) a molecular weight of 10,000 or less, Mw / Mn of 11 to 100 (Mn is the number average molecular weight of the polyethylene resin), and a viscosity average molecular weight (Mv of 100,000 to 1,000,000). And a polyolefin composition containing 8 to 60% of a polyethylene resin and (b) polypropylene, depending on the volume of the component having). This film has a porosity of 20 to 95% and a heat shrinkage of 10% or less at 100 ° C. This microporous polyolefin membrane is formed by extruding a melt blend of the aforementioned polyolefin and a film-forming solvent through a die, stretching the gel-like sheet obtained by cooling, removing the film-forming solvent, and Manufactured by annealing.

  In consideration of the properties of the separator, not only permeability, mechanical strength, shutdown properties, and meltdown properties, but also properties related to heat shrinkability have become important in recent years. Of particular importance in battery manufacture is having a low thermal shrinkage while maintaining high permeability and heat resistance. In particular, the electrode of a lithium ion battery expands or contracts due to the intrusion and release of lithium, and the expansion rate increases as the battery capacity increases. Since the separator is compressed when the electrode expands, it is preferred that the separator when it is compressed resists as little reduction as possible in the electrolyte solution retention.

  Furthermore, although improved microporous membranes are described in JP 6-240036A, WO 1999/48959, WO 2000/20492, WO 2002/072548, and WO 2005/113657, further improvements are required, maintaining high strength and heat resistance. In addition, there is a particular need for microporous membranes that have low thermal shrinkage, good porosity, and uniform high permeability distribution across the microporous membrane. Therefore, it is preferable to produce a battery separator from such a microporous membrane.

  In one embodiment, the present invention relates to a method for producing a microporous membrane having relatively high strength and relatively uniform air permeability, wherein the microporous polymer membrane is in at least one planar direction in a dry orientation zone. Stretching at a high temperature and then heat setting the microporous polymer membrane at least in the first stage and the final stage, where the first stage is upstream of the final stage and the temperature of the first stage is the temperature of the final stage. More than at least 15 ° C., the temperature of the first stage is the same as or higher than the temperature of the dry orientation zone.

  The invention also relates to membranes produced by such methods. If the film comprises polyethylene, the temperature of the dry orientation step should be in the range of 40 ° C. below the temperature from Tcd to Tcd. The first heat setting stage must not be higher than, for example, 10 ° C. above the crystal dispersion temperature of polyethylene.

  The membrane is formed by a plurality of pairs of tenter clips that move from upstream to downstream along at least one planar direction, e.g., along a pair of continuous rails or grooves, during a dry orientation, e.g., in one or two axes. A film is gripped and stretched along its edge. The configuration of the groove determines the direction and the amount of stretching. In some embodiments, the microporous polymer membrane is also gripped during heat setting to adjust for changes in membrane width during the heat setting process. The width of the membrane can be kept constant or reduced during the heat set, for example, by adjusting the pair of tenter clips to reduce the width of the membrane. Thus, in certain embodiments, the present invention relates to heat setting the microporous polymer membrane at least in the first and final stages, where the first stage is upstream of the final stage and the temperature of the first stage is final. At least 15 ° C. below the stage temperature, the microporous polymer membrane has an initial size in at least one planar direction (eg, transverse direction “TD”) after dry blending but before heat setting, It has a final size after planar heat setting, which is smaller in the range of 5-20% than the initial size.

In some embodiments, the microporous polymer membrane is produced by a process comprising: (1) a mixture of a polyolefin composition and at least one diluent, eg, a film-forming solvent, eg, a polyolefin solution. a step of forming a polyolefin composition (a) 1.0x10 weight average molecular weight of less than ⁶ (Mw), e.g., from about 2.5 × 10 ⁵ to about 9 × 10 ⁵ range, and from about 3 to about 100 range from about 50 to about 100% of the first polyethylene resin having a molecular weight distribution (MWD), (b) 1x10 6 or more Mw, for example, about 1.1 × 10 ⁶ to about 5x10 ⁶ range, and from about 3 to about 100 from about 0 to about 40% of the second polyethylene resin having a range of MWD, (c) Mw of about 5x10 ⁵ or more ranges, MWD of from about 1 to about 100 range And about 0 to about 50% polypropylene resin having a heat of fusion of 90 J / g or more, each percentage based on the weight of the polyolefin composition, and (2) extruding the mixture through a die to form an extrudate. (3) cooling the extrudate to form a cooled extrudate having a high polyolefin content; (4) stretching from about Tcd to about Tm of the cooled extrudate of the combined polyethylene. A step of stretching an extruded product cooled in at least one direction at a temperature to form a stretched sheet, and (5) a step of removing at least a part of the diluent or solvent from the stretched sheet to form a film. (6) The film is stretched and expanded in a dry orientation zone, for example, from about 1.1 to about 2 times in at least one direction, and at elevated temperatures (eg, Tc d) and a step of forming a film stretched in (7) and (6), and heat-setting the film product stretched in steps (7) and (6) to form a microporous film. The heat setting is performed in at least two stages. The at least one previous (upstream) heat setting stage is different from the temperature of one or more subsequent (downstream) stages and is performed at a lower temperature, the temperature of the first heat setting stage being the same as the temperature of the drawing zone Or higher.

In certain embodiments, the invention relates to a microporous membrane comprising a polyolefin, the membrane comprising:
(a) The machine direction (MD) in the plane of the membrane and the thickness direction perpendicular to both the plane and the longitudinal direction of the membrane
(b) The lateral width W perpendicular to both the thickness direction and the longitudinal direction, the value of W being determined before the film is cut.
(c) A plurality of air permeation values in the thickness direction of each point along the lateral direction from the first point to the last point, and the standard deviation of the air permeation value does not exceed 20 seconds (i) the first point And the final point is laterally the same distance from point W / 2, and
(ii) The distance between the first point and the last point measured along the lateral direction is at least 75% of W and includes at least one of the following (d) to (f):
(d) Puncture strength of 3,500 mN / 20 μm or more
(e) TD heat shrinkage ratio is 10% or less at 105 ° C
(f) TD heat shrink ratio is 30% or less at 130 ° C.

In certain related embodiments, the microporous membrane has a TD heat shrinkage ratio of 10% or less at 105 ° C, a TD heat shrinkage ratio of 15% or less at 130 ° C, or a molten state of 10% or less at about 140 ° C. Having at least one of the TMA contractions. The microporous membrane may be a polymerized membrane, and the polymerized membrane may include polyethylene, polypropylene, or both. For example, the membrane may include:
(A) 1.0x10 weight average molecular weight of less than ⁶ (Mw), e.g., to about 50 with a 2.5 × 10 ⁵ to about 9 × 10 ⁵ in the range of Mw, and from about 3 to about 100 molecular weight distribution in the range of (MWD) about 100% of the first polyethylene resin, (b) 1x10 ⁶ or more Mw, for example, has a MWD of about 1.1 × 10 ⁶ to 5x10 ⁶ range Mw of, and from about 3 to about 100 range from about 0 to about 40% second polyethylene resin, (c) Mw in the range of about 5 × 10 ⁵ or more, MWD in the range of about 1 to about 100, and about 0 to about 50% polypropylene resin having a heat of fusion of 90 J / g or more. Yes, each percentage is based on the mass of the membrane.

  The microporous membrane of the present invention may be a microporous polymer membrane. In this case, the meaning of “polymerization” means “including one or more polymers”. In addition to the polymer, the polymerized film may optionally include other components, such as organic and / or inorganic materials such as filler materials. If the microporous polymer membrane includes a polyolefin and optionally other components, it can also be referred to as a polyolefin membrane. The term polymer is used herein in a broad sense and includes, for example, any product of a polymerization reaction such as an oligomer, polymer, copolymer, etc., including homopolymer, copolymer, terpolymer, etc. Including. The term “copolymer” refers to a polymer formed by the polymerization of at least two different monomers. For example, the term “copolymer” includes ethylene and alpha-olefins (α-olefins), such as propylene or 1-hexene, which is merely an illustrative example, but includes a copolymerization reaction product of . However, the term “copolymer” includes, for example, the copolymerization of a mixture of ethylene, propylene, 1-hexene, and 1-octene.

  Microporous membranes that benefit from the stepped heat setting process of the present invention include microporous membranes produced by a “wet” manufacturing process, which is a polymer (and to help impart porosity to the membrane). A diluent or solvent is optionally used in addition to the other components. However, the present invention is not limited to such a membrane. For example, the step heat set process of the present invention can also be applied to a microporous membrane produced in a “dry” process, eg, a process that uses a polymer and optionally other materials, but does not use significant amounts of diluents or solvents. Applied.

The microporous membrane used in the stepwise heat treatment process of the present invention is produced by a wet method from an extrudate of a polyolefin solution containing polyolefin and a diluent, and the resin used to form the polyolefin solution is, for example, the following: May include:
(A) 1.0x10 weight average molecular weight of less than ⁶ (Mw), e.g., from about 2.5 × 10 ⁵ to about 9 × 10 ⁵ range, for example, a weight average molecular weight in the range of from about 4.5 × 10 ⁵ to about 6.5 × 10 ⁵ ( Mw) and a first molecular weight of about 50 to about 100%, such as about 50 to about 80%, having a molecular weight distribution (MWD) in the range of about 3 to about 100, such as about 3.5 to about 20. polyethylene resin, (b) 1x10 ⁶ or more Mw, for example, about 1.1 × 10 ⁶ to about 5x10 ⁶ range, for example, about 1.5 × 10 ⁶ to about 3x10 ⁶ range of Mw, and from about 3 to about 100 range E.g., about 0 to about 40%, e.g., about 10 to about 30% of a second polyethylene resin having an MWD in the range of about 3 to about 20, (c) in the range of about 5 x 10 < ⁵ > or more, e.g. about 8x10 To about 1.5x10 ⁶ range Mw, of from about 1 to about 100 range, e.g., above MWD and 90 J / g in the range of from about 2 to about 50, for example, heat of fusion of from about 100 to about 120 J / g From about 0 to about 50%, such as from about 0 to about 40% polypropylene resin. The microporous membrane may preferably contain 50% or less (for example, 0 to 45% or 5 to 45%) of polypropylene obtained from polypropylene resin based on the mass of the microporous membrane and from polypropylene resin. The resulting polypropylene may contain 50% or more (for example, 55 to 100% or 55 to 95%) by mass.

Detailed Description of the Invention

In the case of polymer membranes, it has been observed that relatively high heat set temperatures are required to produce microporous membranes having relatively high air permeability and relatively high puncture strength. For example, in the case of a microporous membrane containing polyethylene, the air permeability normalized to a film thickness of 20 μm is ≦ 300 sec / 100 cm ³ (Gurley value), and the pin puncture strength normalized to a film thickness of 20 μm is ≧ 3500 mN. In order to produce a microporous polymer membrane, the heat set temperature needs to be from about 90 ° C. to about 127 ° C., and it has been observed that lower heat set temperatures require a relatively long time. It was.

  As a practical matter, setting a longer heat setting time at a relatively low heat setting temperature is not preferable because the productivity of the production line is lowered. It was also observed that the pin puncture strength of the microporous membrane was relatively low when the heat setting temperature was relatively low. Increasing the heat setting temperature improved the productivity and pin puncture strength, but it was found that the uniformity of the air permeability deteriorated particularly near the end of the microporous membrane. In particular, when a relatively high heat setting temperature (for example, about 127 ° C. in the case of a microporous membrane containing polyethylene) is used, the film moves from one end to the other end as compared to the standard deviation of the Gurley value before heat setting. It was recognized that the standard deviation of the air permeability (Gurley value) measured at a plurality of points along the TD direction of the microporous membrane was significantly deteriorated.

  Although not intending to be bound by theory or model, it is thought that the deterioration of the standard deviation of the Gurley value is caused by non-uniform residual deformation in the microporous membrane, particularly non-uniform residual deformation in the TD direction before the heat setting process. . In the case of a microporous membrane produced by a wet process, residual deformation is caused by, for example, non-uniform shear applied to the polyolefin solution when the polyolefin solution passes through the die during extrusion, and non-uniform deformation distribution in the wet drawing process (for example, pantograph). This occurs when the attached tenter clip grips the end of the membrane), non-uniform heat distribution during stretching and / or drying (eg, hot spots), or non-uniform deformation distribution during the dry stretching process. In the case of a microporous membrane produced by a dry process, residual deformation is caused by a die shape during sheet molding and non-uniformity during dry stretching.

  Part of this invention is that the dry setting is followed by heat setting of the microporous membrane in at least two stages, where the initial (upstream) stage temperature is set to be higher than the final (downstream) stage temperature. By making the temperature lower by at least 15 ° C. and making the initial stage temperature the same as or higher than the dry stretching zone, the pin puncture strength and air permeability uniformity of the microporous membrane (multiple points along the TD direction) This is based on the discovery that the standard deviation of the air permeability Gurley value measured in (1) can be remarkably improved.

  The dry stretching and the stepwise heat setting according to the present invention can be applied not only to a microporous membrane manufactured by a wet process but also to a microporous membrane manufactured by a dry process. In one embodiment, the microporous membrane is a single layer membrane. The selection of the production method is not important, and any method that can form a microporous membrane from a known polymer starting material, such as the methods disclosed in US Pat. No. 5,051,183 and US Pat. No. 6,096,213, which are incorporated herein by reference, Any method can be used. In another embodiment, the microporous membrane is a multilayer membrane, i.e., a membrane comprising at least two layers. For the sake of brevity, the production of the microporous membrane will be described with reference to a single layer polymer microporous membrane produced primarily by a wet process. However, one skilled in the art will understand that the stepwise heat setting method can be applied to the production of a membrane or a membrane having two or more layers.

[1] Raw Material Used for Production of Microporous Membrane (1) Polyolefin Composition In one embodiment, the present invention provides important physical properties including excellent porosity, low heat shrinkage, and uniform permeability distribution throughout the membrane. The present invention relates to a method for producing a microporous polymer membrane film having a good balance and maintaining high permeability and heat resistance, and having good mechanical strength and compressibility. The microporous polymer membrane is made from one or more polymer resins and a diluent or solvent. When using one or more polymer resins, such as one or more polyolefin (eg polyethylene) resins, the polymer (eg polyolefin) composition is prepared by combining the resins, for example, by melt blending, dry mixing, and the like.
For the sake of brevity, the present application describes the production of a microporous polyolefin membrane, but the invention is also applicable to other microporous membranes.

The polyolefin composition may be, for example, (a) Mw <1 × 10 ⁶ , for example in the range of about 2.5 × 10 ⁵ to about 9 × 10 ⁵ , with a first polyethylene resin having an MWD of about 3 to about 100 from about 50. About 100%, (b) a second polyethylene resin having an MWD of about 3 to about 100 in the range of Mw ≧ 1 × 10 ⁶ , eg about 1.1 × 10 ⁶ to about 5 × 10 ⁶ , about 0 to about 40 And (c) Mw ≧ 5 × 10 ⁵ , polypropylene having an MWD of about 1 to about 100 and a heat of fusion of 90 J / g or more comprises about 0 to about 50%. Here, the percentage is based on the total mass of the polyolefin composition.

  The molecular weight distribution of the polymer composition may be, for example, within a relatively narrow range of about 2.5 to about 7.

  The polyolefin resin will be described in more detail.

(a) Polyethylene Resin In one embodiment, the microporous polyolefin membrane is made from at least one polyethylene resin, i.e., a first polyethylene resin.

(I) Composition The first polyethylene resin has a Mw <1 × 10 ⁶ , for example in the range of about 2.5 × 10 ⁵ to about 9 × 10 ⁵ and an MWD of about 3 to about 100. As a non-limiting example of a first polyethylene resin used in the present application, the Mw is about 2.5 × 10 ⁵ to about 9 × 10 ⁵ , such as 4.5 × 10 ⁵ to 6.5 × 10 ⁵ and the MWD is about 3 From about 5 to about 20, such as from about 4 to about 10. The first polyethylene resin may be an ethylene homopolymer, or ethylene and propylene, butene-1, pentene-1, hexene-1, 4-methylpentene-1, octene-1, vinyl acetate, methyl methacrylate, or It may be an ethylene / α-olefin copolymer comprising styrene or a comonomer selected from a combination thereof ≦ 5 mol%. Such a copolymer is preferably produced using a single site catalyst. Although not essential, the first polyethylene may have two or more terminal unsaturated groups, for example, for 10,000 carbon atoms of the polyethylene. The terminal unsaturated group can be measured, for example, by a known infrared spectroscopy.

When using a second polyethylene resin, for example, an ultra high molecular weight polyethylene (UHMWPE) resin with Mw ≧ 1 × 10 ⁶ , eg, about 1.1 × 10 ⁶ to about 5 × 10 ⁶ and MWD of about 3 to about 100 is used. be able to. Non-limiting examples of second polyethylene resins used in the present application have a Mw in the range of about 1.5 × 10 ⁶ to about 3 × 10 ⁶ , for example about 2 × 10 ⁶ and an MWD of about 3.5 to about 20. Is mentioned. The second polyethylene resin may be an ethylene homopolymer, or ethylene and propylene, butene-1, pentene-1, hexene-1, 4-methylpentene-1, octene-1, vinyl acetate, methyl methacrylate, or It may be a copolymer composed of styrene or a comonomer selected from a combination thereof ≦ 5 mol%. Such a copolymer is preferably produced using a single site catalyst.

(Ii) Molecular weight distribution of polyethylene The MWD of the entire polyethylene composition used in this application is preferably from about 2 to about 300, for example from about 5 to about 50. When the MWD exceeds 100, the proportion of the low molecular weight component becomes too high, and the strength of the resulting microporous film is lowered, which is not preferable. The MWD of polyethylene (homopolymer or polyethylene / α-olefin copolymer) can be controlled by multistage polymerization. The multi-stage polymerization method is preferably a two-stage polymerization method in which a high molecular weight polymer component is produced in the first stage and a low molecular weight polymer component is produced in the second stage. In the polyethylene composition used in the present application, the difference in Mw between high molecular weight polyethylene and low molecular weight polyethylene increases as the MWD increases, and vice versa. The MWD of the polyethylene composition can be appropriately controlled by adjusting the molecular weight and mixing ratio of each component.

(B) Polypropylene resin Although not essential, the microporous membrane can be produced from polyethylene and polypropylene.

(I) Composition The polypropylene resin used in the present application has Mw ≧ 5 × 10 ⁵ , for example, about 8 × 10 ⁵ to about 1.5 × 10 ⁶ , and has a heat of fusion of 90 J / g or more. 100 to about 120 J / g and a molecular weight distribution from about 1 to about 100, such as from about 2 to about 50, or from about 2 to about 6. Polypropylene is a homopolymer of propylene, such as propylene, ethylene, butene-1, pentene-1, hexene-1, 4-methylpentene-1, octene-1, vinyl acetate, methyl methacrylate, styrene, etc., or butadiene, It may be a copolymer (random or block) composed of a comonomer selected from diolefins such as 1,5-hexadiene, 1,7-octadiene, 1,9-decadiene and the like <10 mol%.

  The amount of polypropylene resin in the polyolefin composition is 50% or less based on 100% by mass of the polyolefin composition. When the proportion of polypropylene exceeds 50% by mass, the strength of the resulting microporous membrane is lowered. The proportion of polypropylene resin in the polyolefin composition is from about 0 to about 50% by weight, such as from about 0 to about 40% by weight, for example from about 0 to about 30% by weight.

In one embodiment, the Mw of the polypropylene resin is about 0.8 × 10 ⁶ to about 1.5 × 10 ⁶ , such as about 0.9 × 10 ⁶ to about 1.4 × 10 ⁶ , and the MWD is about 1 To about 100, such as about 2 to about 50, and the heat of fusion is about 80 J / g or more, such as about 90 to about 120 J / g. Optionally, the polypropylene may have one or more of the following physical properties: (i) The polypropylene is isotactic. (Ii) The heat of fusion of the polymer composition is greater than about 108 J / g, or greater than about 110 J / g, or greater than about 112 J / g. (The heat of fusion of the polymer composition can be determined, for example, by a known method such as differential scanning calorimetry (DSC).) (Iii) The melting peak (second melting) is at least about 160 ° C. (Iv) The polypropylene Trouton ratio measured at a temperature of about 230 ° C. and a strain rate of 25 seconds ⁻¹ is at least about 15. (V) The elongational viscosity measured at a temperature of about 230 ° C. and a strain rate of 25 seconds ⁻¹ is at least about 50,000 Pa seconds. (Vi) The high temperature melting point (Tm) is, for example, higher than about 166 ° C, alternatively higher than about 168 ° C, alternatively higher than about 170 ° C. (The melting point can be determined by a known method such as differential scanning calorimetry (DSC).) (Vii) The molecular weight is greater than about 1.75 × 10 ⁶ , or greater than about 2 × 10 ⁶ , or Greater than about 2.25 × 10 ⁶ , for example, greater than about 2.5 × 10 ⁶ . (Viii) The melt flow rate (MFR) at 230 ° C. and a load of 2.16 kg is less than about 0.01 dg / min. (That is, the value is so small that MFR cannot be measured substantially. The melt flow rate can be measured by a known method such as American Society for Testing and Materials (ASTM) Part D 1238-95, Condition L). .) (Ix) The stereoregularity defect is less than about 50 per 10,000 carbon atoms, or less than about 40, or less than about 30, or less than about 20, for example, polypropylene is less than about 10 per 10,000 carbon atoms. Or having a stereoregularity of less than about 5. (X) The meso pentad fraction is greater than about 96 mol% mmmm pentad. And / or (xi) the extract (extracted from polypropylene in boiling xylene) is less than 0.5%, less than 0.2%, less than 0.1% by weight of the polypropylene.

<Measurement of melting point>
Differential scanning calorimetry (DSC) data can be collected by PerkinElmer Instrument, model Pyris 1DSC. A sample weighing approximately 5.5-6.5 milligrams is sealed in an aluminum sample pan. The DSC data is recorded when the sample is first heated to 200 ° C. at a rate of 150 ° C./min, called first melting (data not recorded). The sample is placed at 200 ° C. for 10 minutes, followed by a cooling-heating cycle. The sample is then cooled from 200 ° C. to 25 ° C. at a rate of 10 ° C./min. This is called crystallization. The sample is then placed at 25 ° C. for 10 minutes and then heated to 200 ° C. at a rate of 10 ° C./min. This is called the second melting. Record the thermal behavior during both crystallization and second melt. The melting point (Tm) is the peak temperature in the second melting curve, and the crystallization temperature (Tc) is the peak temperature of the crystallization peak.

<Measurement of meso-pentad-fraction and amount of extracted components>
¹³ C NMR data is collected at 100 MHz and 125 ° C. using a Varian VXR400 NMR spectrometer. Measure with 90 ° C. pulse, acquisition time 3.0 seconds, and pulse delay 20 seconds. The spectrum is decoupled broadband and is measured without gated decoupling. The same relaxation time and nuclear overhauser effect are believed to occur for the polypropylene methyl group resonance, which is the only homopolymer resonance normally used for quantification. The number of transients collected in the measurement is usually 2500. Samples in tetrachloroethane -d _2, is dissolved so that 15 wt%. Measure for all spectral frequencies using a tetramethylsilane internal standard. In the case of polypropylene homopolymer, the resonance of the 21.81 ppm mmmm methyl group is measured which is close to 21.855 ppm which is the value of the tetramethylsilane internal standard reported in the literature. The assignment of the pentads used is known.

  The amount of the extraction component (for example, low molecular weight and / or amorphous substance such as amorphous polyethylene) is determined from the solubility in xylene at 135 ° C. by the following procedure. Weigh 2 grams of sample (which can be pellets or granules) into a 300 ml conical flask. Xylene 200 is placed in a conical flask with a stir bar, and the flask is placed in a heated oil bath. Turn on the heated oil bath and place the flask in a 135 ° C. oil bath for 15 minutes to dissolve the polymer. When the polymer is dissolved, heat is turned off and stirring is continued during cooling. Allow the dissolved polymer to cool naturally overnight. The precipitate is filtered off with Teflon filter paper and dried at 90 ° C. under vacuum. The amount of xylene-soluble matter is obtained by subtracting the weight of the precipitate (B) at room temperature from the weight of the total polymer sample (A), and is obtained in weight percent [soluble matter = ((A−B) / A) × 100]. .

<Measurement of MWD of polyethylene and polypropylene>
Polyethylene and polypropylene Mw and MWD are available at High Temperature Size Exclusion Chromatograph with Differential Refractometer (DRI) or “SEC” (GPC PL220, Polymer Laboratories) Use to measure. The measurement is performed according to the method described in “Macromolecules”, Vol. 34, No. 19, pages 6812-6820 (2001). For the measurement of Mw and MWD, three PLgel Mixed-B columns manufactured by Polymer Laboratories are used. In the case of polyethylene, the apparent flow rate is 0.5 cm / min, the apparent injection volume is 300 μL, and the transfer line, column, and DRI meter are placed in an oven maintained at 145 ° C. In the case of polypropylene, the nominal flow rate is 1.0 cm / min, the nominal injection volume is 300 μL, and the transfer line, column, and DRI meter are placed in an oven maintained at 160 ° C.

  As the GPC solvent to be used, Aldrich reagent grade 1,2,4-trichlorobenzene (TCB) containing 1000 ppm of butylated hydroxytoluene (BHT) is used after filtration. The TCB was degassed with an online degasser before entering the SEC. This solvent was used in the SEC eluate. For the polymer solution, the dried polymer was placed in a glass container, a predetermined amount of TCB solvent was added, and then the mixture was stirred for about 2 hours while continuously heating at 160 ° C. The concentration of the polymer solution was 0.25 to 0.75 mg / ml. Before injecting the sample solution into GPC, it was filtered off-line with a 2 μm filter using SP260 Model Sample Prep Station (manufactured by Polymer Laboratories).

  The separation efficiency of a set of columns is a calibration curve generated using 17 polystyrene standard samples with Mp (Mp is defined as the peak of Mw) in the range of about 580 to about 10,000,000. And calibrated. Polystyrene standard samples were obtained from Polymer Laboratories (Amherst, Mass.). A calibration curve (logMp vs. retention capacity) was generated by measuring the retention capacity of the peak in the DRI signal of each PS standard sample and fitting this data to a second order polynomial. Samples were analyzed using IGOR Pro manufactured by Wave Metrics, Inc.

(2) Other components In addition to the above components, the polyolefin solution includes (a) additional polyolefin, and / or (b) a heat-resistant resin having a melting point or glass transition temperature of 170 ° C. or higher, and a microporous membrane The heat resistant resin may be contained in such an amount that the physical properties (such as puncture strength and air permeability) are not lowered, for example, 10% by mass or less with respect to the polyolefin composition.

(A) Additional polyolefins Additional polyolefins are: (a) polybutene-1, polypentene-1, poly-4-methylpentene-1, polyhexene-1, polyoctene-1, with Mw from 1 × 10 ⁴ to 4 × 10 ⁶ ; Polyvinyl acetate, polymethyl methacrylate, polystyrene and ethylene / α-olefin copolymer, and (b) Mw is at least one of polyethylene wax having 1 × 10 ³ to 1 × 10 ⁴ . Polybutene-1, polypentene-1, poly-4-methylpentene-1, polyhexene-1, polyoctene-1, polyvinyl acetate, polymethyl methacrylate, and polystyrene need not be homopolymers; It may be a copolymer.

(B) Heat-resistant resin Examples of heat-resistant resins are: (a) a partially crystalline amorphous resin having a melting point of 170 ° C. or higher, (b) a completely amorphous resin having a melting point of 170 ° C. or higher, and a mixture thereof. is there. The melting point and Tg can be measured by differential scanning calorimetry (DSC) according to JISK7121. Examples of heat-resistant resins include polyesters such as polybutylene terephthalate (melting point: about 160-230 ° C), polyethylene terephthalate (melting point: about 250-270 ° C), fluorine resin, polyamide (melting point: 215-265 ° C), polyarylene sulfide, Tg: 280 ° C. or higher), polyamideimide (Tg: 280 ° C.), polyethersulfone (Tg: 223 ° C.), polyether ether ketone (melting point: 334 ° C.), polycarbonate (melting point: 220-240 ° C.), cellulose acetate ( Melting point: 220 ° C., cellulose triacetate (melting point: 300 ° C.), polysulfone (Tg: 190 ° C.), polyetherimide (melting point: 216 ° C.) and the like.

(C) Content The amount of additional polyolefin and heat resistant resin is preferably 20% or less, for example from about 0 to about 20%, based on 100% of the mass of the polyolefin solution.
[ 2] Production of microporous membrane

For the sake of brevity, the production of the microporous membrane has been described in terms of a wet process, but the invention is not limited thereto. Thus, in one embodiment, the present invention provides
(1) combining a particular polyolefin (generally in the form of a polyolefin resin) and at least one diluent, eg, a solvent, to form a mixture, eg, a polyolefin solution;
(2) a step of extruding the mixture through a die to form an extrudate,
(3) a step of cooling the extrudate to form a cooled extrudate,
(4) stretching the cooled extrudate at a specific temperature to form a stretched sheet;
(5) removing at least a portion of the diluent from the stretched sheet;
(6) Stretching the film in a dry orientation zone to form a film from which the diluent has been removed, and (7) Heat setting the film product of step (6) to form a microporous film. Wherein the heat setting is performed in at least two stages, wherein at least one early heat setting stage is performed at a temperature different from and lower than the temperature of the one or more late heat setting stages. The present invention relates to a method for producing a microporous membrane comprising the steps of: The heat setting treatment step (4i), the hot roll treatment step (4ii), and / or the hot solvent treatment step (4iii) may be performed between steps (4) and (5) as desired. Subsequent to step (7), a cross-linking step (8) having ionizing radiation, hydrophilization step (8i) and / or surface coating treatment step (8ii) is optionally carried out after step (7). Also good.
(1) Preparation of polyolefin solution

  The polyolefin resin can be combined with at least one diluent to prepare a mixture. Alternatively, a plurality of polyolefin resins may be combined into a polymer composition, for example by melt blending, dry mixing, etc., which is then combined with at least one diluent to prepare a mixture. The mixture optionally contains various additives such as antioxidants, fine silicate powders (pore-forming substances), etc. in amounts that do not cause deterioration of the properties of the microporous membrane produced from this mixture. It may be contained in an amount generally less than 5% by weight based on the weight of the mixture.

  In order to be able to stretch at a relatively high magnification, the diluent, for example a film-forming solvent, is preferably liquid at room temperature. Liquid solvents are, for example, aliphatic, cycloaliphatic or aromatic hydrocarbons such as nonane, decane, decalin, p-xylene, undecane, dodecane, liquid paraffin, mineral oil distillate having a boiling point equivalent to the boiling point of these hydrocarbons. And phthalates that are liquid at room temperature, such as dibutyl phthalate, dioctyl phthalate, and the like. In order to more effectively obtain extrudates with a stable solvent content, non-volatile liquid solvents such as liquid paraffin can be used. In one embodiment, one or more solid solvents that are miscible with the polyolefin composition, for example during melt blending, but are solid at room temperature, may be added to the liquid solvent. Such a solid solvent is preferably stearyl alcohol, seryl alcohol, paraffin wax or the like. In other embodiments, the solid solvent can be used without a liquid solvent. However, if only a solid solvent is used, it may be more difficult to evenly stretch the extrudate.

  The viscosity of the liquid solvent is preferably about 30 to about 500 cSt, more preferably about 30 to about 200 cSt, when measured at a temperature of 25 ° C. If the viscosity at 25 ° C. is less than 30 cSt, the polyolefin solution may foam, and as a result, blending may become difficult. On the other hand, if the viscosity exceeds 500 cSt, it may be difficult to remove the liquid solvent.

  Although not particularly essential, uniform mixing of the polyolefin solution is preferably carried out in a twin screw extruder to prepare a highly concentrated polyolefin solution. Diluent may be added prior to initiating mixing, or may be fed to the middle section of the twin screw extruder during mixing. However, the latter is preferred.

  The mixing (eg, melt blending) temperature of the polyolefin solution is preferably in the range of the melting point (“Tm”) of the polyolefin resin + 10 ° C. to Tm + 120 ° C. The melting point can be measured by differential scanning calorimetry (DSC) according to JIS K7121. In one embodiment, the melt blending temperature is from about 140 ° C to about 250 ° C, more preferably from about 170 ° C to about 240 ° C, especially when the polyolefin resin has a melting point of from about 130 ° C to about 140 ° C.

  In one embodiment, the concentration of the polyolefin composition in the polyolefin solution is preferably about 15 to about 50% by weight, more preferably about 20 to about 45% by weight, based on the weight of the polyolefin solution.

  The ratio L / D between the screw length L and screw diameter D of the twin screw extruder is preferably in the range of about 20 to about 100, more preferably in the range of about 35 to about 70. If L / D is less than 20, melt blending may become inefficient. When L / D is more than 100, the residence time of the polyolefin solution in the twin screw extruder may be too long. In this case, as a result of excessive shearing and heating, the molecular weight of the membrane deteriorates, which is undesirable. The cylinder of the twin screw extruder preferably has an inner diameter of about 40 to about 100 mm.

In the twin screw extruder, the ratio Q / Ns between the amount Q (kg / hour) of the polyolefin solution charged and the rotational speed Ns (rpm) of the screw is preferably about 0.1 to about 0.55 kg / hour / hour. rpm. If Q / Ns is less than 0.1 kg / hr / rpm, the polyolefin may be damaged by shearing, and the strength and meltdown temperature may decrease. When Q / Ns is more than 0.55 kg / hr / rpm, uniform blending cannot be achieved. Q / Ns is more preferably about 0.2 to about 0.5 kg / hr / rpm. The rotation speed Ns of the screw is preferably 180 rpm or more. Although not particularly essential, the upper limit of the screw rotation speed Ns is preferably about 500 rpm.
(2) Extrusion

The components of the polyolefin solution can be melt blended in an extruder and extruded from a die. In other embodiments, the components of the polyolefin solution can be extruded and then pelletized. In this embodiment, the pellets can be melt blended in a second extruder and extruded into a gel-like molding or sheet. In either embodiment, the die can be a sheet forming die having a rectangular base, a double cylindrical hollow die, an inflation die, or the like. Although the die gap is not critical, in the case of sheet forming dies, the die gap is preferably from about 0.1 to about 5 mm. The extrusion temperature is preferably from about 140 to about 250 ° C. and the extrusion rate is preferably from about 0.2 to about 15 m / min.
(3) Formation of cooled extrudate

  The extrudate from the die is cooled to form a cooled extrudate, which is generally in the form of a high polyolefin content gel-like molding or sheet. Cooling is preferably performed at a cooling rate of about 50 ° C./min or more, at least to the gel temperature. Cooling is preferably performed to about 25 ° C. or less. Such cooling creates a polyolefin microphase separated by a film-forming solvent. In general, a slower cooling rate results in a gel-like sheet with larger pseudocell units, resulting in a coarser higher order structure. On the other hand, higher cooling rates result in denser cell units. When the cooling rate is less than 50 ° C./min, the degree of crystallinity increases, and it may be more difficult to obtain a gel-like sheet having suitable stretchability. Cooling methods suitable for use include contacting the extrudate with a cooling medium such as cooling air, cooling water, etc., and contacting the extrudate with a chill roll or the like.

High polyolefin content means that the cooled extrudate is at least about 15%, such as about 15 to about 50%, based on the mass of the cooled extrudate, of polyolefins derived from the resin of the polyolefin composition. It means to include. If the polyolefin content is less than about 15% or more than 50% of the cooled extrudate, it may be more difficult to form a microporous membrane. The cooled extrudate preferably has a polyolefin content that is at least as high as the polyolefin content of the polyolefin solution.
(4) Stretching of the cooled extruded product

  The cooled extrudate, generally in the form of a high polyolefin content gel or sheet, is then stretched in at least one direction. Although not wishing to be bound by any theory or model, it is believed that the gel-like sheet can be uniformly stretched because it contains a diluent or solvent. The gel-like sheet is preferably stretched to a predetermined magnification after being heated by, for example, a tenter method, a roll method, an inflation method, or a combination thereof. Stretching can be performed uniaxially or biaxially, but biaxial stretching is preferred. In the case of biaxial stretching, any of simultaneous biaxial stretching, sequential stretching or multistage stretching (for example, a combination of simultaneous biaxial stretching and sequential stretching) can be used, but simultaneous biaxial stretching is preferred. The amount of stretching in either direction need not be the same.

  In the case of a uniaxial direction, the draw ratio of this drawing step can be, for example, 2 times or more, preferably 3 to 30 times. In the case of biaxial stretching, the stretching ratio can be, for example, 3 times or more in any direction, that is, the area magnification is 9 times or more, such as 16 times or more, such as 25 times or more. An example of this stretching step would include about 9 to about 49 times stretching. Again, the amount of stretching in either direction need not be the same. If the area magnification is 9 times or more, the puncture strength of the microporous membrane is improved. If the area magnification is, for example, more than 400 times, the stretching device, stretching operation, etc. require a large-scale stretching device, which may be difficult to operate.

  In order to obtain a good microporous structure, the stretching temperature of this stretching step is relatively high, preferably from the approximate crystal dispersion temperature (“Tcd”) of the total polyethylene content of the cooled extrudate to the approximate melting point. (“Tm”), for example, in the range of Tcd to Tm of the total polyethylene-containing material. If the stretching temperature is lower than Tcd, the total polyethylene-containing material is not sufficiently softened, so that the gel-like sheet is easily broken by stretching and high-strength stretching cannot be achieved.

  The crystal dispersion temperature is determined by measuring the temperature characteristics of dynamic viscoelasticity according to ASTM D4065. Since the total polyethylene content of the present invention has a crystal dispersion temperature of about 90-100 ° C, the stretching temperature is about 90-125 ° C, preferably about 100-125 ° C, more preferably 105-125 ° C.

  The above stretching causes tearing between lamellae of polyolefins such as polyethylene, making the polyolefin phase finer and forming a large number of fibrils. Fibrils form a three-dimensional network structure. Stretching is thought to improve the mechanical strength of the microporous membrane and enlarge its pores, making it suitable for use as a battery separator.

Depending on the desired properties, stretching having a temperature distribution in the thickness direction is performed, and a microporous membrane having improved mechanical strength can also be obtained. A detailed description of this method is given in US Pat. No. 3,347,854.
(5) Removal of solvent or diluent

A washing solvent is used for the purpose of removing (washing out, replacing or dissolving) at least a part of the solvent or diluent. Since the phase of the polyolefin composition is phase separated from the diluent or solvent phase, removal of the solvent or diluent results in a microporous membrane. Removal of the solvent or diluent can be carried out by using one or more suitable washing solvents, i.e. washing solvents capable of transferring the liquid solvent from the membrane. Examples of washing solvents are volatile solvents such as saturated hydrocarbons such as pentane, hexane, heptane, chlorinated hydrocarbons such as methylene chloride, carbon tetrachloride, ethers such as diethyl ether, dioxane and the like, ketones such as methyl ethyl ketone. Linear fluorocarbons such as trifluoroethane, C ₆ F _{14 and the} like, cyclic hydrofluorocarbons such as C ₅ H ₃ F _{7 and the} like, hydrofluoroethers such as C ₄ F ₉ OCH ₃ , C ₄ F ₉ OC ₂ H _{5 and the} like, perfluoroethers such as C ₄ F ₉ OCF ₃ , C ₄ F ₉ OC ₂ F _{5 and the} like and mixtures thereof.

  Cleaning the stretched membrane can be performed by dipping in the cleaning solvent and / or showering the cleaning solvent. The washing solvent used is preferably about 300 to about 30,000 parts by weight per 100 parts by weight of the stretched membrane. The washing temperature is usually about 15 to about 30 ° C., and heating may be performed during washing if desired. The heating temperature during washing is preferably about 80 ° C. or less. Washing is preferably performed until the amount of residual liquid diluent or solvent is less than about 1% by weight of the amount of liquid solvent that was present in the polyolefin solution prior to extrusion.

The microporous membrane from which the diluent or solvent has been removed is dried by a heat drying method, an air drying method (for example, air drying using moving air) or the like, and residual volatile components such as a washing solvent are removed from the membrane. be able to. Any drying method capable of removing a significant amount of the washing solvent can be used. Preferably, substantially all of the washing solvent is removed during drying. The drying temperature is preferably equal to or lower than Tcd, more preferably 5 ° C. or more lower than Tcd. Drying is carried out until the residual washing solvent is preferably less than 5 wt.%, More preferably less than 3 wt.% Per 100 wt.% (On a dry basis) of the microporous membrane. Insufficient drying is undesirable, and subsequent heat treatment can lead to a decrease in the porosity of the microporous membrane, resulting in unsatisfactory permeability.
(6) Re-stretching of the film

  The film from which the diluent or solvent has been removed and / or dried is stretched at a predetermined magnification in at least a uniaxial direction within the stretching zone. Since this stretching step occurs after stretching of the extrudate, it may be referred to as a “second” stretching step, a “restretching” step, or more commonly a “dry orientation” step. Dry orientation can be carried out according to conventional methods such as those described, for example, in WO2008 / 016174 and WO2007 / 117042, the contents of which are hereby incorporated by reference in their entirety. It is captured. The restretching of the membrane can be carried out as in the first stretching step (4), for example, at an elevated temperature, such as by a tenter method. Re-stretching may be uniaxial stretching or biaxial stretching. In the case of biaxial stretching, simultaneous biaxial stretching or sequential stretching can be used, but simultaneous biaxial stretching is preferred. Re-stretching is usually carried out on a membrane in the form of a long sheet obtained from a stretched gel-like sheet, so that the MD and TD directions in re-stretching (MD is the “machine direction”, ie while the film is being processed, The direction of travel is meant, and TD means the “transverse direction”, ie the direction perpendicular to both the MD and horizontal planes of the membrane.) Is usually the same as the direction in stretching of the cooled extrudate. Although not required, the expansion factor for redraw can be somewhat greater than the expansion factor used for drawing the cooled extrudate. The draw ratio of this step can be in at least one direction, such as from about 1.1 to about 2 times, such as from about 1.2 to about 1.6 times. Stretching need not be the same magnification in each direction. Moreover, the stretch during dry orientation can be used to compensate for the stretch of the extrudate. For example, if the draw ratio used in step (4) is at or near the lower end of the draw range, the draw ratio used in step (6) is in the range of about 1.1 to about 2, for example 1.5. It can be a relatively high value. Similarly, if the draw ratio used in step (4) is at or near the lower end of the draw range, the draw ratio used in step (6) is in the range of about 1.1 to about 2, for example 1. It can be a relatively low value of less than 5.

  The dry orientation (second stretching or restretching) step is performed in a stretching zone, which has a Tcd or less range, for example, a range of Tcd-40 ° C to Tcd, or a range of Tcd-20 ° C to Tcd. There may be two stretching temperatures. When the second stretching temperature is higher than Tcd, the membrane shrinks in a significant amount in the direction perpendicular to MD and TD during redrawing, resulting in low permeability and large properties over the TD direction of the membrane. It is thought that the distribution of When the second stretching temperature is lower than Tcd-40 ° C., the polymer in the film is insufficiently softened. As a result, the film may be broken by stretching, that is, it may not be possible to achieve uniform stretching. Conceivable. In embodiments where the polymer comprises polyethylene, the second stretching temperature can range from about 60 ° C to about 100 ° C, such as from about 70 ° C to about 100 ° C.

  The uniaxial stretching ratio of the film in this step (6) is preferably about 1.1 to about 2 times as described above. A magnification of 1.1 to 2 times results in a membrane of the invention having a structure with a generally large average pore size. In the case of uniaxial stretching, the magnification can be 1.1 to 2 times in the longitudinal or transverse direction. In the case of biaxial stretching, the membrane can be stretched at the same or different magnifications in each stretching direction. But as long as the draw ratio in both directions is 1.1 to 2 times or less, the same ratio is preferable.

  If the second draw ratio of the membrane is less than 1.1 times, the membrane structure of the present invention is considered to have unsatisfactory permeability and compression resistance of the membrane. It is considered that when the second draw ratio is more than 2 times, the fibrils formed are too fine, and thus the heat shrink resistance of the film is reduced. This second draw ratio is preferably about 1.2 to about 1.6 times.

The stretching speed is preferably 3% / second or more in the stretching direction. In the case of uniaxial stretching, the stretching speed is 3% / second or more in the longitudinal direction or the transverse direction. In the case of biaxial stretching, the stretching speed is 3% / second or more in both the longitudinal direction and the transverse direction. A stretch rate of less than 3% / second reduces the permeability of the membrane and results in a membrane with large non-uniform properties (especially air permeability) in the width direction when stretched in the transverse direction. The stretching speed is preferably 5% / second or more, more preferably 10% / second or more. Although not particularly essential, the upper limit of the stretching speed is preferably 50% / second in order to prevent rupture of the film.
(7) Heat treatment

  The film product of step (6) is heat-treated (heat set) to a predetermined width in a heat setting step having at least two stages. Heat setting the film is thought to stabilize the crystal and create a uniform lamella in the film. The heat setting step is generally performed with the end of the membrane fixed to the desired width. Conventional methods such as tenter methods or roll methods can be used. The heat set temperature for each stage is preferably in the range of about 20 ° C. below Tcd (“Tcd−20 ° C.”) to Tm. Furthermore, at least one early (upstream) heat setting stage is performed at a temperature that is different from and lower than the temperature of the other late (downstream) heat setting stage. Still further, the first stage heat set is about 10 ° C. (10 ° C. hotter than Tcd) or less (“Tcd + 10 ° C.”) below about Tcd, preferably about Tcd-10 ° C. to about Tcd. Performed at a range of temperatures. The temperature difference between the first stage (ie, “first” or most upstream heat setting stage) and the last stage (ie, “final” or most downstream heat setting stage) is about 15 ° C. or more The temperature is preferably about 20 ° C. or higher, more preferably 25 ° C. to 40 ° C. or higher. In one embodiment, at least three heat setting stages are used. In other embodiments, at least 5 heat setting stages are used. The first heat setting stage is downstream of the dry orientation zone of step (6). The temperature of the first heat setting stage must be the same or higher (hot) than the dry orientation zone (or the downstream end if there is a temperature gradient within the dry orientation zone).

  Using a heat set temperature that is too low may make it more difficult to produce a film with adequate pin puncture strength, tensile rupture strength, tensile rupture elongation, and heat shrink resistance, while using a heat set temperature that is too high. It may be more difficult to produce a sufficiently permeable membrane.

  The membrane is heat set for a total time over all stages generally ranging from about 1 to about 200 seconds, typically from 20 to about 90 seconds, for example from about 25 to about 80 seconds. The time per stage can be selected independently. For example, each heat set time at each stage can range from 0.2 to 195 seconds, or from about 5 to about 50 seconds. In one embodiment, the polymer microporous membrane comprises a polyolefin, such as polyethylene, or polyethylene and polypropylene, and the temperature of the first heat setting stage is no higher than 10 ° C. above the Tcd of polyethylene. In general, the heat setting stage is arranged from upstream to downstream with no process steps in between, but this is not essential. For example, one or more roll stages, such as a heated roll stage, can be used during the heat setting stage.

  Heating a polymer microporous membrane generally causes membrane size shrinkage. During heat setting, the end of the membrane is gripped by, for example, a tenter clip that secures the end of the membrane, and the tendency to shrink during heating creates tension in the plane of the membrane, which tension Restrained by gripping clip pairs located at opposite ends. A pair of clips is typically incorporated along a pair of opposing, continuous rails (one at each end of the membrane) or as desired as the membrane progresses along the production line from downstream to upstream along the machine direction. Clip closing / opening means are provided so that the heat setting process can be operated continuously. The rail or track is set so that the tenter clip follows a path that keeps the film width constant during the heat setting phase, or a path that results in a decrease in film size, eg, TD, MD, or both MD and TD. Can. For example, the clip path may range from about 1% to about 30%, or about 5% to about 20% less than the initial width (TD), from the initial width before heat setting to the final size. It can be a pathway that causes a decrease in the membrane.

  In one embodiment, the membrane comprises polyethylene, or polyethylene and polypropylene, and the temperature of the first heat setting stage is 20 ° C. below the Tcd of polyethylene (20 ° C. cooler than Tcd), but in dry orientation Same or hotter than the zone temperature. Optionally, the temperature of each series of heat setting stages is the same or higher than the temperature of the preceding heat setting stage. For example, one embodiment has five heat setting stages: an upstream (or first) stage, a second stage immediately downstream of the first stage, a third stage immediately downstream of the second stage, It has a fourth stage immediately downstream of the third stage and immediately upstream of the final stage, and a downstream (or final) stage. The temperature of each stage can increase monotonically and then level off, for example the temperature of the first stage is for example in the range of 85 ° C. to 95 ° C., for example 90 ° C .; The range of 95 ° C to 115 ° C, for example 100 ° C or 110 ° C; the temperature of the third stage is, for example, in the range of 115 ° C to 125 ° C, for example 110 ° C or 120 ° C; For example, in the range 115 ° C. to 127 ° C., for example 127 ° C .; and the final stage temperature is in the range of 120 ° C. to 127 ° C., for example 127 ° C.

  The term “stage temperature” means the average temperature within the stage, for example, placing thermocouples at various points inside the stage (generally along the machine direction) and then the thermoelectric It can be measured by taking the numerical average (arithmetic mean) of the paired values.

In one embodiment, the polymer microporous film (a) less than 1x10 ^6, for example, about 2.5 × 10 ⁵ ～9X10 first polyethylene resin about 50 to about of having Mw and about 3 to about 100 of MWD of ⁵ range 80%, (b) 1x10 ⁶ or more, such as about 1.1 × 10 ⁶ ~ about 3x10 ⁶ second polyethylene resin about 10 to about 30% with Mw and about 3 to about 100 of MWD ranging, and (c) Polypropylene resin having a Mw of ⁵ × 10 ⁵ or more, such as in the range of about 8 × 10 ⁵ to about 1.5 × 10 ⁶ and a MWD of about 1 to about 100 and a heat of fusion in the range of 80 J / g or more, such as in the range of about 100 to about 120 J / g. Contains about 0 to about 40%, these percentages being based on the weight of the polyolefin composition. The following table contains examples of selected heat setting conditions for films made from such polyolefin compositions.

  In one embodiment, the temperature of the extension zone is in the range of 70 degrees to 90 degrees Celsius, the temperature in the starting stage is in the range of 90 degrees to 127 degrees Celsius, the temperature in the second stage is in the range of 120 degrees to 127 degrees Celsius, The temperature of the third and fourth stages is in the range of 125 degrees to 127 ° C.

  As stated with respect to step (6), dry stretching is characterized by a change in the planar area of the membrane from the initial size to the final size. This change in size can be accomplished by fixing the end of the membrane with a pair of opposing tenter clips that move on a pair of continuous rails or tracks. When the rails are placed away from each other, the distance between the facing tenter clips increases and the membrane stretches. The downstream end of the dry stretching process can be defined as the point at which the membrane no longer extends, for example, when the distance between the pair of rails no longer increases. Heat setting of the film at a fixed size (or smaller) at the end of the dry stretching process can begin immediately after the end of the dry stretching process. Although not necessary, the dry stretching zone and the heat setting stage can be provided in one processing apparatus. For example, the tenter device can be placed in an enclosure (e.g., substantially insulated) that is divided into parts that perform independent temperature management (each part is substantially isothermal).

  The heat setting in each heat setting step can be performed under the conventional heat setting conditions. Two such conditions are referred to as “thermal fixation” or “thermal relaxation”. The term “heat setting” refers to a heat set performed while maintaining the stretch ratio selected during dry stretching, for example by a tenter clip. The term “thermal relaxation” means that heat setting is performed so that the elongation ratio is smaller than the elongation during dry stretching, for example, by a pair of tenter clips facing each other.

  In some embodiments, the heat setting process can be performed continuously. In another embodiment, the heat setting process is performed semi-continuously or intermittently. For example, the film can be heat-set after dry stretching of the film and then a suitable time. Although not necessary, the amount of film width reduction can be determined separately for each heat setting step. The trajectory of the tenter clip has a final magnification of about 0.7 to about 0.99 times compared to the size of the film (eg, at the beginning of the heat setting step (7)) in the stretching direction in the heat setting step. , It can be determined that the membrane relaxes (ie shrinks) in the stretched direction. The film can be relaxed at a ratio of about 1% to about 30%, preferably about 5% to about 20% less than the size of the film at the beginning of the heat setting step (7). The membrane can relax in TD, MD or both directions.

  It has been discovered that the heat setting process gives the microporous membrane more uniform and high permeability throughout the membrane. After the heat setting step, the microporous membrane has a standard deviation of permeability in the TD direction (for example, about 10 to about 15 (seconds) or less) and a thermal shrinkage rate in the TD direction of 105% or less at 105 ° C. (for example, About 0.5% to about 5% or less), 10% or less of heat shrinkage in the TD direction at 130 ° C. (for example, about 10% to about 25% or less), and puncture strength of 3,500 mN or more.

  An annealing process can be performed after a heat setting process. Annealing can be performed using a heating chamber with a belt conveyor or an air floating type heating chamber, for example, in that no force or load is applied to the microporous membrane. Annealing can also be done by loosening the tenter clip following the heat setting. The annealing temperature is preferably below Tm, more preferably in the range of about 60 ° C to about Tm-5 ° C. Annealing is believed to improve the permeability and strength of the microporous membrane.

  Optionally, the stretched sheet can be heat set between steps (4) and (5). This heat setting method can be performed in the same manner as described above for step (7), but this is not necessary and a conventional single heat setting can be used.

  Furthermore, at least one surface of the stretched sheet in step (4) may contact one or more heater rollers after any of steps (4) to (7). The temperature of this roller is preferably in the range of Tcd + 10 ° C. to Tm. The contact time between the stretched sheet and the heating roll is preferably about 0.5 seconds to about 1 minute. This heated roll may have a smooth or rough surface. This heating roll may have a suction function to remove the solvent. Although not particularly important, an example of a roller heating system may include holding heated oil on the surface of the roller.

Further, the stretched sheet may come into contact with a hot solvent between steps (4) and (5). The high-temperature solvent treatment changes a group of small fibers formed by stretching into a vein-like shape with a relatively thick fiber trunk, and gives a microporous membrane having large pores and appropriate strength and permeability. The term “leaf vein shape” refers to a group of small fibers having a thick fiber trunk and thin fibers extending from the trunk into a complex network. Details of the high temperature solvent treatment method are described in WO 2,000 / 20,493.
(8) Cross-linking

The heat-set microporous membrane can be crosslinked by ionizing radiation such as α-rays, β-rays, γ-rays, and electron beams. When emitting an electron beam, the amount of electron beam is preferably about 0.1 to about 100 Mrad, and the acceleration voltage is preferably about 100 to about 300 kV. Crosslinking treatment increases the meltdown temperature of the microporous membrane.
(8i) Hydrophilization treatment

  The heat-set microporous membrane may be subjected to a hydrophilic treatment (a treatment for making the membrane more hydrophilic). The hydrophilization treatment may be monomer grafting treatment, surfactant treatment, corona discharge treatment or the like. The monomer grafting treatment is preferably performed after the crosslinking treatment.

In the case of a surfactant treatment for hydrophilizing a heat-set microporous membrane, any of a nonionic surfactant, a cationic surfactant, an anionic surfactant and an amphoteric surfactant can be used. Ionic surfactants are preferred. The microporous membrane can be quickly immersed in an aqueous solution of a surfactant or a lower alcohol such as methanol, ethanol, isopropyl alcohol, etc., and can be coated with this solution by the doctor blade method.
(8ii) Surface coating treatment

Although not necessarily required, the heat-set microporous membrane that has undergone the step (6) is a porous polypropylene, a porous fluororesin, such as a porous polypropylene resin, for example, to improve the melt-down property when the membrane is used as a battery separator. It can be coated with polyvinylidene fluoride, polytetrafluoroethylene, porous polyimide, porous polyphenylene sulfide and the like. The polypropylene used in the coating preferably has a solubility of about 5,000 to about 500,000 Mw, at least about 0.5 grams in 100 grams of toluene at 25 ° C. Such polypropylene preferably has a racemic diad in a proportion of about 0.12 to about 0.88. Racemic diads are structural units in which two adjacent monomer units are mirror image isomers of each other. For the surface coating layer, for example, the above-mentioned coating resin solution dissolved in a good solvent is used for the microporous membrane, and part of the solvent is removed to increase the resin concentration, thereby separating the resin phase and the solvent phase. Can be made by forming a structure that will then remove the remainder of the solvent. For this reason, examples of good solvents include aromatic compounds such as toluene or xylene.
[3] Structure, properties and composition of microporous membrane
(1) Structure

  The microporous membrane of the present invention is a porous membrane having a composition derived from the polymer resin used to make this membrane. As used herein, the term “pore size” is like the diameter of a pore when the pore is substantially cylindrical. The thickness of the membrane is generally in the range of about 1 to 100 μm, usually 5 to 50 μm.

The microporous membrane of the present invention has a relatively large internal space and pores due to the coarse domain, so that when compressed, the air permeability hardly changes, and suitable permeability and electrolyte absorption It has. The microporous membrane also has relatively small internal spaces and pores that, when used as battery separators, affect membrane safety such as shutdown temperature and shutdown speed. Therefore, a lithium ion battery, for example, a lithium ion secondary battery including a separator formed of such a microporous film has suitable productivity and cycleability while maintaining high safety performance.
(2) Properties

  The microporous membrane of the present invention has a standard deviation of air permeability of less than 15 seconds (standardized to a membrane thickness of 20 μm) between points across the membrane along the TD, for example about Standard deviation of 5 to about 15 seconds or less and one or more of the following properties: 10% TD thermal shrinkage at 105 ° C, eg, about 0.5 to about 5%, 30 ° C or less at 130 ° C TD direction heat shrinkage ratio, for example, about 25% or less, puncture strength of 3,500 mN or more, and thickness fluctuation (absolute value) after heating and compression of less than 10, preferably 9 or less.

  The membrane exiting the heat setting process is deformed along the edges due to the tenter clip sandwiching the membrane. Generally, this portion of the membrane is removed by cutting the portion of the membrane near the edge into a strip. This ablation can be performed continuously. For example, by placing a cutting blade in the machine direction at the desired distance, inward (along TD) from the edge of the membrane. The end piece material is cut out and removed from the process. In general, this process of slitting (slitting) reduces the width of the film after the heat setting process from about 90% to about 95%. This slitting process can be referred to as the “first” slitting process, for example, when another slitting is used in the downstream process to manufacture a microporous membrane having a predetermined final width for battery manufacturing. .

  The air permeability of the membrane passing through the membrane can be measured at a position selected along TD (ie, the direction across the entire membrane). Except where otherwise different from the context, the term “air permeability” as used herein refers to the arithmetic average (ie, number average) of measurements. Although not necessarily required, measurement points spaced approximately equal along TD and multiple measurement points on the membrane centerline (parallel to the machine direction) determine air permeability and standard deviation of air permeability. used. Since the measurement point is at the center line of the membrane, the measurement can be performed before or after slitting.

  In one embodiment, the selected air permeability measurement point is located along the TD and between the start and end points, the start and end points being any equidistant along the TD from the membrane centerline. . The distance between the starting point and the final point is, for example, about 75% of the width of the membrane after heat setting and before slitting (ie before any slitting downstream of the first slitting or the first slitting), Or about 80%, or about 90%, or about 95%. Air permeability and standard deviation of air permeability can only be determined by the start and end points, but usually these points and points along the TD are used to determine these values. The For example, 5 points or more, 10 points or more, 20 points or more, or 40 points or more are used. For example, the number of measurement points is in the range of 10 to 30 points, and these points can optionally be equally spaced along the TD at convenient intervals, eg between adjacent measurement points The distance may be in the range of about 25 mm to about 100 mm.

The term “μ” refers to the arithmetic mean (Gurley value, measured in seconds per 100 cm ³ ) of air permeability determined at measurement points along TD. The standard deviation “σ” of the measured air permeability is defined as the square root of the variation. That means
σ = (Σ (AP−μ) ² / N) ^1/2 , where AP is the measured air permeability (Gurley value) at each measurement point, and N is the number of measurement points.

  The membrane is characterized by a heat shrinkage value measured at 105 ° C., which can be measured as follows. A sample of the microporous membrane is cut along TD and MD to obtain a square sample having sides of 100 mm (that is, 100 mm in the TD direction and 100 mm in the MD direction). The sample is then heated for 8 hours at a temperature of 105 ° C. (in an oven) to reach thermal equilibrium and then cooled. The shrinkage in MD (expressed as a percentage) is equal to the percentage of the sample in the MD direction before heating divided by the length of the sample in the MD direction after heating multiplied by 100. The shrinkage in TD direction (expressed as a percentage) is equal to the percentage of the length of the sample in the TD direction before heating divided by the length of the sample in the TD direction after heating multiplied by 100.

  The membrane can also be characterized by heat shrinkage measured at 130 ° C. This value is particularly important because 130 ° C. is generally within the operating temperature range of the lithium ion secondary battery during charging and discharging (almost close to the upper limit (shutdown temperature) of this range). This measurement is slightly different from the measurement of heat shrinkage at 105 ° C., where the edge of the membrane parallel to the transverse direction is generally fixed in the cell, especially in the vicinity of the center of the edge parallel to the machine direction. Or it reflects the fact that shrinkage is limited. Thus, a square sample of microporous film that is 50 mm along TD and 50 mm along MD will fix the edge parallel to TD to the frame (eg, with tape), leaving a space of 35 mm in the MD direction, and TD The direction leaves a space of 50 mm. The frame with the sample is then heated and heated for 30 minutes at 130 ° C. with thermal equilibration and then cooled. TD heat shrinkage generally causes the end of the film parallel to the MD to bend slightly inward (in the direction of the center of the frame space). TD shrinkage (expressed as a percentage) is the percentage of the sample in the TD direction before heating divided by the shortest length of the sample in the TD direction (inside the frame) multiplied by 100 equal.

  When the heat shrinkage after exposure to 105 ° C for 8 hours exceeds 10% in the transverse direction, the heat generated in the battery having the microporous membrane separator can cause the separator to shrink. Make it easy to cause a short circuit in the vicinity. Similarly, when the heat shrinkage ratio after exposure to 130 ° C. for 30 minutes exceeds 30% in the transverse direction, the heat generated in the battery using this microporous membrane separator causes a short circuit near the end of the separator. Make it easier. The heat shrinkage is preferably about 0.5 to about 5% at 105 ° C and about 10% to about 55% at 130 ° C.

  Microporous membranes generally have a shutdown temperature of 140 ° C. or lower and a meltdown temperature of 145 ° C. or higher. The meltdown temperature is measured by the following procedure. A 3 mm × 50 mm rectangular sample is cut out from the microporous membrane so that the long axis of the sample is aligned with the transverse direction of the microporous membrane as manufactured in the process and the short axis is aligned with the machine direction. This sample is set in a thermomechanical analyzer (TMA / SS6000 available from Seiko Instruments, Inc.) with a fixed distance of 10 mm (ie, the distance from the upper fixation to the lower fixation is 10 mm). The The lower part is fixed, and a load of 19.6 mN is applied to the upper part. Fixing device and sample are placed in a heatable tube. Beginning at 30 ° C, the temperature inside the tube increases at a rate of 5 ° C / min, and under a load of 19.6 mN, the change in sample length as the temperature increases is measured at 0.5 second intervals. And recorded. The temperature rises to 200 ° C. The meltdown temperature of the sample is defined as the temperature at which the sample breaks and is generally in the range of about 145 ° C to about 200 ° C. In particular, commercial grade battery separators preferably have a meltdown temperature of 145 ° C or higher, ie, have a meltdown temperature of 145 ° C or higher.

  The maximum shrinkage in the molten state is measured by the following procedure. Using the meltdown temperature measurement procedure, the sample length measured in the temperature range of 135 ° C. to 145 ° C. is recorded. The maximum shrinkage in the molten state is the length of the sample between the fixtures measured at 23 ° C (L1 is 10mm) minus the shortest length (L2), typically measured in the range of about 135 ° C to about 145 ° C. The value divided by L1, that is, [L1-L2] / L1 × 100%. In particular, commercial grade battery separators have a thermomechanical analysis maximum shrinkage of 30% in the molten state at 140 ° C., with a lower percentage being preferred, ie 20% or less.

In a preferred embodiment, the microporous membrane of the present invention also has at least one of the following properties.
(A) Air permeability of about 20 to about 400 seconds / 100 cm ³ (converted to a value at a thickness of 20 μm)

When the air permeability of the measured film by JIS P8117 is 400 sec / 100 cm ^3/20 [mu] m to 20, batteries with separators formed by the microporous membrane is suitably, a large capacity and good cyclability Have. When the air permeability is less than 20 sec / 100 cm ^3/20 [mu] m, when the temperature in the battery rises above 140 ° C., since the shutdown is sufficiently pore can not be sufficiently close so the pore is very large Does not happen. The air permeability P ₁ measured for a microporous membrane having a thickness T ₁ in accordance with JIS P8117 is converted to an air permeability P ₂ at a thickness of 20 μm by the formula, P ₂ = (P ₁ x20) / T ₁ ( That is, it is standardized). The air permeability can be measured at a plurality of points along the TD. The standard deviation of the measured value is equal to the square root of the variation. Air permeability, which is converted to a value corresponding to a film thickness of 20 [mu] m is expressed in units of [seconds / 100cm ³ / 20μm]. The air permeability can be measured at a plurality of points along the TD. The standard deviation of the measured value is equal to the square root of the variation. Air permeability, which is converted to a value corresponding to a film thickness of 20 [mu] m is expressed in units of [seconds / 100cm ³ / 20μm].
(B) Porosity of from about 25 to about 80%

  When the porosity is less than 25%, the microporous membrane is generally less useful as a battery separator. It is believed that when the porosity exceeds 80%, the battery separator formed with a microporous membrane has insufficient strength and can cause a short circuit of the battery electrodes.

The porosity is measured by a gravimetric method using the following formula. Porosity% = 100 × (w2−w1) / w2, where “w1” is the actual weight of the film and “w2” is the expected weight of 100% polyethylene.
(C) Puncture strength (pin puncture) of 3,500 mN or more (value converted to a value at a thickness of 20 μm )

The membrane puncture strength (converted to a 16 μm thick membrane value) is 1 mm in diameter with a microporous membrane having a spherical end surface (radius of curvature R: 0.5 mm) at a rate of 2 mm / sec. Expressed by the maximum load measured when struck by the needle. If the puncture strength is low (eg, less than 3,500 mN / 20 μm), it is generally more difficult to produce a battery that provides sufficient protection against internal short circuits. The puncture strength is preferably 4,000 mN / 16 μm or more, for example, 4,500 mN / 20 μm or more. Puncture strength measurements can be made at multiple locations along the TD and averaged. The standard deviation of the measured value is equal to the square root of the variation.
(D) Tensile strength of 100,000 kPa or more

Tensile strength (measured by ASTM D-882 using a 10 mm wide rectangular test piece) in both the machine direction and the transverse direction is suitable for use as a battery separator. This is a characteristic of the microporous membrane. The tensile strength at break is preferably about 100,000 kPa or more, for example, about 135,000 kPa or more.
(E) Tensile elongation of 100% or more

Tensile elongation (measured by ASTM D-882 using a 10 mm wide rectangular test piece) in both the machine direction and the transverse direction is a microscopic product with suitable durability, especially when used as a battery separator. This is a characteristic of the porous membrane.
(F) Fluctuation rate of 20% or less thickness after heating (absolute value)

  The variation rate of the thickness after heating and compression at a pressure of 2.2 MPa for 5 minutes at 90 ° C. is generally 20% or less (when expressed as an absolute value) with respect to 100% of the thickness before compression. The thickness can be measured as shown in (h) below. The variation rate of the thickness is calculated by the formula of (average thickness after compression−average thickness before compression) / (average thickness before compression) × 100.

A battery including a microporous membrane separator having a thickness variation rate of 20% or less, preferably 10% or less, has an appropriately large capacity and good cycleability.
(G) Air permeability after heating and compression of 700 seconds / 100 cm ³ or less

Each microporous membrane having a thickness T ₁ is heated and compressed under the above conditions and measured for air permeability P _{1 according} to JIS P8117.

When heated and compressed under the above conditions, the microporous membrane generally has an air permeability (Gurley value) of 700 seconds / 100 cm ³ or less. A battery using such a membrane has a reasonably large capacity and cycleability. The air permeability is preferably 675 seconds / 100 cm ³ or less.
(H) Average thickness (μm)

  The thickness of each microporous membrane is measured and averaged with a contact thickness meter at an interval of 5 cm in the vertical direction for a width of 30 cm. The standard deviation of the measured value is equal to the square root of the variation.

The thickness measuring instrument used is Litematic manufactured by Mitsutoyo Corporation. The thickness of the membrane is generally in the range of about 1 to 100 μm, usually 10 to 100 μm.
(3) Microporous membrane composition

The microporous polymer membrane is composed of a resin or a polymer of a plurality of resins used for the production of the membrane. If this membrane is made by a wet process, it may typically contain a small amount of washing and / or processing solvent in an amount of less than 1 wt% based on the weight of the microporous polymer membrane. The polymer molecular weight degrades slightly during the process, but is acceptable. In embodiments where the polymer is a polyolefin and the membrane is produced in a wet process, the molecular weight may decrease during processing, but the MWD value of the polyolefin of the membrane relative to the MWD of the polyolefin solution, if any. Is only about 50%, or about 1%, or only about 0.1%.
Polyolefin

One embodiment of the microporous membrane of the present invention is (a) less than 1 × 10 ⁶ , ie, in the range of about 2.5 × 10 ^{5 to} about 9 × 10 ⁵ , eg, about ^4.5 × 10 ^{5 to} about 6.5 × 10 ⁵ Mw and about 3 to about 100, for example, it has a 3.5 to about 2.5 of MWD, from about 50 to about 100% of the first polyethylene, (b) 1x10 ⁶ or more Mw (e.g., about 1.1 × 10 ⁶ to about 5x10 ⁶ , eg, 1.5 × 10 ^{6 to} about 3 × 10 ⁶ ) and about 3 to 100, eg, about 0 to about 40% of second polyethylene having an MWD of about 3.5 to about 20, and (c) 5 × 10 ⁵ above, for example, 8x10 ⁵ to 1.5 × 10 ^6, the Mw and about 1 to 100, for example, from about 2 to about 50, or from about 2 to about 6 MWD, and 90 J / g or more, for example, to about 100 to about 120 / G with a heat of fusion, of about 0 to about 50% polypropylene. The percentage is based on the membrane capacity.
(A) Polyethylene
(I) Composition

The first polyethylene has an Mw of less than 1 × 10 ⁶ , for example, in the range of about 2.5 × 10 ^{5 to} about 9 × 10 ⁵ and an MWD of about 3 to 100. Non-limiting examples of the first polyethylene for use herein, those having from about 4.5 × 10 ⁵ to about 6.5 × 10 ⁵ of Mw and about 3.5 to about 20 or from about 4 to about 10 of MWD is there. The first polyethylene may be an ethylene homopolymer or a copolymer of ethylene and up to 5 mol% comonomer. The copolymer is selected from propylene, butene-1, pentene-1, hexene-1, 4-methylpentene-1, octene-1, vinyl acetate, methyl methacrylate, or styrene, or combinations thereof. Such a copolymer is preferably produced using a single site catalyst.

Second polyethylene, for example, ultrahigh molecular weight polyethylene (UHMWPE) used in any, 1x10 ⁶ or more, for example, 1.1 × 10 ⁶ to about 5 to 10 ⁶ in the range of Mw (WMD definitely) and about 3 to about 100 With an MWD in the range of One non-limiting example of a second polyethylene as used herein is one having a Mw of about 1.5 × 10 ^{6 to} about 3 × 10 ⁶ and a MWD of about 4 to about 10. The second polyethylene may be an ethylene homopolymer or a copolymer of ethylene and 5 mol% or less of a comonomer, which copolymer is propylene, butene-1, pentene-1, hexene-1, 1,4-methylpentene. -1, octene-1, vinyl acetate, methyl methacrylate, or styrene, or combinations thereof. Such a copolymer is preferably produced using a partial catalyst.
(Ii) Molecular weight distribution (MWD) of polyethylene in a microporous membrane

Although not critical, the MWD of polyethylene in the membrane is preferably from about 3 to about 100, such as from about 3.5 to about 20. If the MWD is less than 3, the percentage of higher molecular weight components is too high, making melt extrusion difficult. On the other hand, when the MWD is 100 or more, the percentage of the lower molecular weight component is increased, and the strength of the obtained microporous membrane is decreased. Some Mw degradation occurs from the starting resin during membrane manufacture by the method of the present invention. For example, the Mw of the first and / or second polyethylene of the membrane product is lower than the Mw of the first and / or second polyethylene ethylene resin in the polyolefin composition of the polyolefin solution of step (1) of the present invention.
(A) Polypropylene
(I) Composition

Polypropylene about 5x10 ⁵ or more, for example, from about 8x10 ⁵ to about 1.5 × 10 ⁶ of the Mw, from about 1 to about 100, for example, from about 2 to about 50 of MWD, and 90 J / g or more, for example, from about 100 to about 120J / G of heat of fusion. The polypropylene may be a propylene homopolymer or a copolymer of propylene and up to 10 mol% comonomer, which is ethylene, butene-1, pentene-1, hexene-1, 4-methylpentene-1, octene-1, acetic acid It is selected from vinyl, methyl methacrylate, styrene and the like, and diolefins such as butadiene, 1,5-hexadiene, 1,7-octadiene and 1,9-decadiene. The percentage of the olefin comonomer in the propylene copolymer is preferably in a range that does not hinder the properties of the microporous membrane such as heat resistance, compression resistance, and heat shrinkage. Furthermore, the Mw of the starting resin is reduced during membrane manufacture by the method of the present invention. For example, the Mw of polypropylene in the film is lower than the Mw of polypropylene in the polyolefin composition portion of the polyolefin solution in step (1) of the present invention.

The heat of fusion is determined by a differential scanning calorimeter (DSC). This DSC is performed using TA Instruments MDSC2920 or Q1000Tzero-DSC, and data is analyzed using general analysis software. Usually 3-10 mg of polymer is enclosed in an aluminum pan and placed in the apparatus at room temperature. The sample is cooled to either -130 ° C or -70 ° C and heated to 210 ° C at a heating rate of 10 ° C / min to evaluate the glass transition temperature and melting properties of the sample. This sample is maintained at 210 ° C. for 5 minutes to break the thermal history. Crystallization properties are evaluated by cooling a sample melted to near room temperature (near room temperature) at a cooling rate of 10 ° C./min. The sample is kept at a low temperature for 10 minutes to fully parallelize the solid state and make it stable. The second melting data is measured by heating the melted and crystallized sample at 10 ° C./min. The second melting data thus provides the phase properties of the crystallized sample under controlled thermal history conditions. The endothermic melting transition (first and second melting) and the exothermic crystallization transition are analyzed for the initiator and peak temperature of the transition. The area under the curve is used to determine the heat of fusion (ΔH _f ).

In one embodiment, the amount of polypropylene in the membrane is no more than 50% of the total volume of polyolefin in the membrane.
Other ingredients

In addition to the aforementioned components, the membranes of the present invention can also include additional polyolefins and / or heat resistant polymers having a melting point or glass transition temperature above about 170 ° C.
(A) Additional polyolefin

Additional polymers include: (a) polybutene-1, polypentene-1, poly-4-methylpentene-1, polyhexene-1, polyoctene-1, polyvinyl acetate, polymethyl methacrylate, polystyrene, and ethylene / alpha olefins copolymer (respectively 1x10 having ⁴ to 4x10 ⁶ of Mw) may in and (b) 1x10 ³ to 1 or more polymethine ethylene wax having Mw of 1x10 ^4. Polybutene-1, polypentene-1, poly-4-methylpentene, polyhexene-1, polyoctene-1, polyvinyl acetate, polymethyl methacrylate, and polystyrene are not limited to homopolymers, but include other alpha olefins. It may be a polymer.
(B) Heat resistant polymer

The heat resistant polymer is preferably (i) an amorphous polymer having a melting point of about 170 ° C. or higher, which may be partially crystalline and / or (ii) an amorphous polymer having a Tg of about 170 ° C. or higher. It is. The melting point and Tg are determined by a differential scanning calorimeter (DSC) based on JISK7121. Examples of heat-resistant polymers include polybutylene terephthalate (melting point: about 160 to 230 ° C.), polyethylene terephthalate (melting point: 250 to 270 ° C.), fluororesin, polyamides (melting point: 215 to 265 ° C.), polyarylene Sulfide, polyimide (Tg: 280 ° C or higher), polyamideimide (Tg: 280 ° C), polyethersulfone (Tg: 223 ° C), polyetheretherketone (melting point: 334 ° C), polycarbonate (melting point: 220 to 240) ° C), cellulose acetate (melting point: 220 ° C), cellulose triacetate (melting point: 300 ° C), polysulfonate (Tg: 190 ° C), polyetherimide (melting point: 216 ° C), and the like.
(C) Content

The total amount of additional polyolefin and heat-resistant polymer in the membrane is preferably 20% or less, assuming that the membrane capacity is 100%.
[4] Battery separator

The microporous membrane of the present invention is useful as a battery separator. In one or more embodiments, the microporous membrane of the present invention has a thickness of about 3 to about 200 μm, or about 5 to about 50 μm, or about 7 to about 35 μm, with the most preferred thickness being the type of battery being manufactured Depends on.
[5] Battery

  Although not important, the microporous membrane of the present invention is used as a separator for primary and secondary batteries, particularly lithium ion secondary batteries, lithium-polymer secondary batteries, nickel-hydrogen secondary batteries, nickel-cadmium disulfide batteries, nickel -It is useful as a separator for a zinc secondary battery, a silver-zinc secondary battery, particularly a lithium ion secondary battery.

  This lithium ion secondary battery includes an anode and a cathode laminated via a separator, and the separator usually includes an electrolyte in the form of an electrolyte solution (electrolyte). The structure of the electrode is not important. A conventional structure is preferred. The electrode structure is, for example, a disc-shaped coin type in which the anode and the cathode are placed opposite to each other, a laminated type in which the anode and the cathode are laminated in a flat shape, and a ribbon-shaped anode and cathode in a donut shape. It is something that is wrapped around.

The anode typically includes a current collector and includes a positive electrode active material layer capable of absorbing and discharging lithium ions formed on the current collector. The positive electrode active material is an inorganic material such as a transition metal oxide, a composite oxide of lithium and a transition metal (lithium composite oxide), or a transition metal sulfide. This transition metal is V, Mn, Fe, Co, Ni or the like. Suitable examples of lithium composite oxides include lithium trivalent composites on thin layers based on lithium nickelate, lithium cobaltate, lithium magnate, α-NaFeO ₂ . The cathode includes a current collector and a negative electrode active material layer formed over the current collector. This negative electrode active material layer is a carbon-based material such as natural graphite, artificial graphite, coke, or carbon black.

This electrolytic solution is a solution obtained by dissolving a lithium salt in an inorganic solvent. This lithium salt is LiClO ₄ , LiPF ₆ , LiAsF ₆ , LiSbF ₆ , LiBF ₄ , LiCF ₃ SO ₃ , LiN (CF ₃ SO ₂ ) ₂ , LiC (CF ₃ SO ₂ ) ₃ , Li ₂ B ₁₀ Cl ₁₀ , LiN (C ₂ F ₅ SO ₂ ) ₂ , LiPF ₄ (CF ₃ ) ₂ , LiPF ₃ (C ₂ F ₅ ) ₃ , lithium lower aliphatic carboxylate, LiAlCl _{4 and the} like. These lithium salts can be used alone or in combination. The organic solvent is an organic solvent having a high boiling point and a high dielectric constant, such as ethylene carbonate, propylene carbonate, ethyl methyl carbonate, γ-butyl carbonate; and / or tetrahydrofuran, 2-methyltetrahydrofuran, dimethoxyethane, dioxolane, An organic solvent having a low boiling point and low viscosity such as dimethyl carbonate and dimethyl carbonate may be used. These organic solvents can be used alone or in combination. Since organic solvents having a high dielectric constant have a high viscosity, and those having a low viscosity usually have a low dielectric constant, it is preferable to use a mixture thereof.

  When assembling the battery, the separator is immersed in the electrolyte to cause ion permeability. This impregnation treatment is usually performed by immersing the microporous membrane in an electrolyte solution at room temperature. When assembling a cylindrical battery, for example, an electrode sheet, a microporous membrane separator, and a negative electrode sheet are laminated in order, and the obtained laminated body is wound around a donut-shaped electrode assembly. The obtained electrode assembly is packed / molded in a battery can, immersed in the above-described electrolytic solution, a battery with a safety valve attached to the end of the positive electrode and a lid is packed in the battery can with a gasket to form a battery.

  All tests, test procedures, and other cited references, including the application on which priority is based, are in all jurisdictions whose disclosures are consistent with the present invention and are incorporated by reference in the law. Which is incorporated herein by reference.

  Although described in exemplary form, it will be understood that other modifications can be readily made by those skilled in the art without departing from the spirit and scope of the invention. That is, the appended claims should not be limited to the examples and various descriptions herein, but include all technical features that are considered equivalent by those skilled in the art to which the present invention pertains. It consists of all the patentable technical features in this specification.

  Numerical lower limit values and upper limit values are listed, but a range combining arbitrary lower limit values and upper limit values is also intended.

The invention is explained in more detail by reference to the following examples. The following examples do not limit the scope of the present application.
Example 1

(A) 80% first polyethylene having Mw of 5.6 × 10 ⁵ and MWD of 4.05, (b) 20% of second polypropylene having Mw of 1.9 × 10 ⁶ and MWD of 5.09, ( A polyolefin composition comprising (c) no polypropylene resin was prepared by dry blending. The percentage is based on the volume of the polyolefin composition. The polyethylene resin in this composition has a melting point of 135 ° C., a crystal dispersion temperature of 100 ° C., and an MWD of 14.4.

  25 parts based on the volume of the resulting polyolefin composition was loaded into a strong blend twin screw extruder having an internal diameter of 58 mm and an L / D ratio of 42, and 70 parts liquid paraffin (50 cst at 40 ° C. at 40 ° C.). ) Was fed to the twin screw extruder through a side feeder. The melt blending was performed at 210 ° C. and 200 rpm to obtain a polyethylene solution. This polyethylene solution was extruded from a T-die installed in an extruder. The extruded product was cooled by passing through a cooling roll adjusted to 40 ° C. to produce a cooled extruded product, that is, a gel-like sheet.

Using a tenter stretcher, the gel-like sheet was stretched 5 times by simultaneous biaxial stretching at 115 ° C. on each of the vertical and horizontal axes. The stretched gel-like sheet is immersed in a methylene chloride bath adjusted to 25 ° C., and the liquid paraffin is removed until the amount of liquid paraffin present in the polyolefin solution is 1% or less by volume. And dried with an air stream. The dried membrane was restretched 1.4 times with a batch stretching machine in the transverse direction at 129 ° C. The dried film is subjected to a tenter type machine by a first step at 90 ° C. for 10 seconds, a second step at 127 ° C. for 10 seconds, a third step at 127 ° C. for 10 seconds, and a fourth step at 127 ° C. for 10 seconds. A microporous membrane was produced by heat setting. The film width in the longitudinal direction in the first three heat setting processes was kept constant. In the final heat setting step, the film was finally reduced by 5% with respect to the longitudinal film width (initial film width) in the first heat setting step.
Example 2

Example 1 was repeated except that the restretching step was performed at 70 ° C.
Example 3

The re-stretching process was performed at 100 ° C., the heat setting process was performed at 100 ° C. for 10 seconds in the second process, and the film width was 15% smaller than the film width at the start of the first heat setting process in the longitudinal direction of the third process. Example 1 was repeated. The film width in the fourth step was kept the same as the film width in the third step. The fourth step was performed at the same temperature as the fourth step of Example 1, but the final film width was shrunk by 20% from the initial film width.
Example 4

Example 3 was repeated except that the restretching step was performed at 90 ° C., the first step of the heat setting step was performed at 90 ° C. for 10 seconds and the second step was performed at 120 ° C. for 10 seconds.
Example 5

Example 1 was repeated except that the film shrinkage in the longitudinal direction in the third step was made 15% smaller than the film width at the start of the first step. The width of the film in the fourth step was the same as the width of the third step. The fourth step was performed at the same temperature as the fourth step of Example 1, but the final film width was 20% smaller than the initial film width.
Example 6

Example 5 was repeated except that the redraw ratio was 1.2 times in the machine direction and the film shrinkage in the machine direction of the third step was 17% smaller than the film width at the start of the first step. The film width in the fourth step was kept the same as the film width in the third step. The fourth step was performed at the same temperature as the fourth step in Example 1.
Example 7

Polyolefin composition comprising polypropylene having 50% primary polyethylene, 20% secondary polyethylene, and 30% molecular weight of 1.1 × 10 ⁶ , molecular weight distribution of 5.0, and / or heat of fusion of 114 J / g Example 4 was repeated except that each heat setting step was performed at 126 ° C. using the product.
Comparative Example 1

Example 1 was repeated except that the restretching and heat setting steps were performed at 127 ° C.
Comparative Example 2

Comparative Example 1 was repeated except that the first heat setting step was performed at 90 ° C.
Comparative Example 3

Comparative Example 1 was repeated except that the film width in the vertical direction of the third step was made 15% smaller than the film width of the first step. The film width in the fourth step was the same as in the third step. In the fourth step, the fourth step of Comparative Example 1 was maintained at the same temperature, but the final film width was 20% smaller than the initial film width.
Comparative Example 4

Comparative Example 3 was repeated except that the heat setting process was all 90 ° C.
Comparative Example 5

Comparative Example 1 was repeated except that the film width in the vertical direction of the third step was made 15% smaller than the film width of the first step. The film width in the fourth step was the same as in the third step. In the fourth step, the fourth step of Comparative Example 1 was maintained at the same temperature, but the final film width was 20% smaller than the initial film width.
Comparative Example 6

Example 1 was repeated except that the restretching step was performed at 50 ° C. The film broke at the time of redrawing.
Comparative Example 7

It was repeated except that all of the re-stretching step and the heat setting step were performed at 126 ° C.
nature

The properties of the multilayer microporous membranes obtained in Examples and Comparative Examples were measured by the method described in Section [3] (2). The results are shown in Table 1.

From Table 1, the microporous membrane of the present ^invention, 100 cm 3 standard deviations of the air permeability of the longitudinal (Gurley) 15 seconds or less per film, 20 to 300 sec / 100 cm ^3/20 [mu] m air permeability, 10% Longitudinal heat shrinkage at 105 ° C., longitudinal heat shrinkage of 30% or less, and TMA maximum shrinkage when melted at about 140 ° C. of 30% or less, puncture strength of 3,500 or more, 10 or less Thickness change after compression, tensile strength (MD and TD) of 125,000 kPa or more, tensile elongation of 150 to 200 (MD and TD direction thickness of 0.18 μm, puncture strength of TD direction of 15 or less, And the air permeability after heat compression of 670 or less, on the other hand, the microporous membrane of the comparative example has poor standard deviation of the air permeability in the TD direction or low puncture strength, and TD and MD. Directional tension Degree is weak, the TD direction of the heat shrinkage at 105 ° C. and 130 ° C. poor, or the thickness variation after heat compression is not preferable.

  The battery separator formed by the microporous polyolefin membrane of the present invention provides suitable safety, heat resistance, storage properties, and productivity.

Claims (23)

A method for producing a microporous membrane, the method comprising:
Stretching the microporous polymer membrane in at least one planar direction in a dry orientation zone at a high temperature and then heat setting the microporous membrane in at least an upstream stage and a downstream stage, wherein the temperature of the upstream stage is The method, wherein the temperature of the upstream stage is at least 15 ° C. lower than the temperature of the downstream stage, and the temperature of the upstream stage is equal to or higher than the temperature of the dry orientation zone. The method of claim 1, wherein the microporous polymer membrane comprises polyethylene and the temperature of the first stage is not higher than 10 ° C above the Tcd of polyethylene. The microporous polymer membrane has an initial size in at least one planar direction before heat setting and has a final size in one planar direction after heat setting, the final size being 5 to 20% of the initial size. The method according to claim 1 or 2, wherein the method is small in the range. The method of claim 1, further comprising performing the following steps prior to the stretching (6) and staged heat setting (7) steps:
(1) A step of combining a polyolefin composition and at least one diluent to form a mixture, wherein the polyolefin composition is (a) a weight average molecular weight (Mw) of less than 1.0 × 10 ^{6 and} a molecular weight of 3 to 100 50 to 100% of a first polyethylene resin having a distribution (MWD), (b) a Mw of 1 × 10 ⁶ or more, 0 to 40% of a second polyethylene resin having a MWD of 3 to 100, (c) about 5 × 10 ⁵ or more. Mw, 1 to 100 MWD, and 0 to 50% polypropylene resin having a heat of fusion of 90 J / g or more, each percentage based on the weight of the polyolefin composition,
(2) a step of extruding the mixture through a die to form an extruded molded product,
(3) a step of cooling the extrudate and forming a cooled extrudate,
(4) forming a stretched sheet by stretching the cooled extrudate in at least one direction at a stretching temperature of from about Tcd ° C. to about Tm ° C. of a cooled extrudate of the combined polyethylene; And (5) a step of removing at least a part of the diluent from the stretched sheet to form a microporous polymer film. 5. The method of claim 4, further comprising at least one of the following steps:
(4i) a heat setting step between steps (4) and (5), wherein the stretched sheet is heat set at a temperature of a stretching temperature ± 5 ° C;
Following the (4i) step and before the (5) step, (4ii) a heated roll treatment step, in which the stretched sheet is heated at a temperature ranging from the Tcd of the polyolefin composition to the melting point of the polyolefin composition + 10 ° C. In contact with the rolled roller;
(4ii) following the step, and (5) before the step (4iii) heating solvent treatment step, contacting the stretched sheet with a heating solvent;
(7) A cross-linking step (8) following the step, wherein the heat-set microporous membrane is cross-linked by ionizing radiation selected from one or more of α rays, β rays, γ rays and electron beams;
(7) Step (8i) is a hydrophilization treatment step, wherein the heat-set microporous membrane is made more hydrophilic by one or more of monomer grafting treatment, surface activated treatment, and corona discharge treatment. Or (8ii) a surface coating treatment step following the step (7), wherein the heat-set microporous membrane is made of porous polypropylene, porous fluorinated resin, porous polyimide, and porous polyphenylene sulfide. Covered by one or more. The heat set has at least a second stage between an upstream stage and a downstream stage, the temperature of the second stage is higher than the upstream stage, the same as or lower than the downstream stage, and the microporous polymer membrane is in all stages. 6. The method of claim 4 or 5, wherein the total time over is set heat in the range of about 1 to about 200 seconds, and expansion by stretching in the stretching zone is in the range of 1.1 to 2. Whether the heat set has a second stage immediately downstream of the upstream stage, and a third stage immediately downstream of the second stage and immediately upstream of the downstream stage, and the temperature of each successive stage is the same as its preceding stage. 6. The method of claim 4 or 5, wherein the microporous polymer membrane is heat set at each stage in the range of about 2 to about 100 seconds. Said polyolefin composition (a) 2.5 × 10 ⁵ to 9 × 10 ⁵ of Mw and 3.5 to the first polyethylene resin in 50 to 80% has a molecular weight distribution of 20 (MWD), (b) 1.1x10 6 to 5x10 10 to 30% second polyethylene resin having a Mw in the range of ⁶ and a MWD of 3.5 to 20, (c) Mw in the range of 8 × 10 ^{5 to} 1.5 × 10 ⁶ , MWD in the range of 2 to 50, 100 8. The method of claim 7, comprising from 0 to 40% polypropylene resin having a heat of fusion of from 120 to 120 J / g, each percentage based on the weight of the polyolefin composition. The temperature of the stretching zone is in the range of 70 ° C to 90 ° C, the temperature of the upstream stage is in the range of 90 ° C to 120 ° C, the temperature of the second stage is in the range of 120 ° C to 127 ° C, and The method of claim 8, wherein the third and fourth stage temperatures range from 125 ° C to 127 ° C. 10. The microporous polymer membrane produced by the method according to any one of claims 1 to 9, wherein the microporous polymer membrane is produced. A microporous membrane comprising polyolefin, wherein the membrane is
(a) Thickness direction perpendicular to the longitudinal direction and both the planar and longitudinal direction of the film in the plane of the film
(b) The lateral width W perpendicular to both the thickness direction and the longitudinal direction, the value of W being determined before the film is cut.
(c) a plurality of air permeability values in the thickness direction of each point along the transverse direction from the first point to the final point, the standard deviation of the air permeability values exceed 15 seconds / 100 cm ^3/20 [mu] m (I) the first and last points are the same distance from point W / 2 along the lateral direction, and
(ii) The distance between the first point and the last point measured along the lateral direction is at least 75% of W and includes at least one of the following (d) to (f):
(d) Puncture strength of 3,500mN / 20μm or more
(e) TD heat shrinkage ratio is 10% or less at 105 ° C
(f) TD heat shrink ratio is 30% or less at 130 ° C.
The microporous membrane comprising: The puncture strength is 4,000mN / 20μm or more, TD heat shrinkage ratio is 5% or less at 105 ° C., or TD thermal shrinkage ratio of 25% or less at 130 ° C., the air permeability of 300 sec / 100 cm ^3/20 [mu] m or less, MD And the TD tensile strength is 125,000 kPa or more, and the absolute value of the variation in thickness after thermal compression is 10% or less. The polyolefin (a) 1.0x10 weight average molecular weight of less than ⁶ (Mw), and 50 to 100% of the first polyethylene resin having a molecular weight distribution in the range of 3 to 100 (MWD), (b) 1x10 6 or more 0 to 40% second polyethylene resin having Mw and 3 to 100 MWD, (c) 5 to 10 ⁵ Mw of 1 to 100 MWD, and 0 to 50% polypropylene having a heat of fusion of 90 J / g or more 13. A microporous membrane according to claim 11 or 12, comprising a resin, each percentage based on the mass of the membrane. The microporous membrane is
(A) 2.5 × 10 ⁵ to 9x10 weight average molecular weight of ⁵ (Mw) and 3.5 to 50 to 80% of the first polyethylene resin having a molecular weight distribution of 20 (MWD), (b) 1.1x10 6 to 5x10 10 to 30% second polyethylene resin having ⁶ Mw and 3.5 to 20 MWD, (c) 8 × 10 ^{5 to} 1.5 × 10 ⁶ Mw, 1 to 100 MWD, and 100 to 120 J / g 14. The microporous membrane of claim 13, comprising from 0 to 40% polypropylene resin having a heat of fusion of, each percentage based on the mass of the membrane. The first polyethylene is one or more of an ethylene homopolymer or an ethylene / α-olefin copolymer, the second polyethylene is one or more of an ethylene homopolymer or an ethylene / α-olefin copolymer, and the polypropylene is a propylene homopolymer. 14. The microporous membrane of claim 13, which is one or more of a polymer or a propylene / α-olefin copolymer. The membrane further comprises polybutene-1, polypentene-1, poly-4-methylpentene-1, polyhexene-1, polyoctene-1, polyvinyl acetate, polymethyl methacrylate, polystyrene, and an ethylene / α-olefin copolymer. The microporous membrane according to claim 11 or 12, comprising one or more of them. (1) at least one of the number of the points is at least 20, the standard deviation of air permeability value does not exceed 18 seconds / 100 cm ^3/20 [mu] m, and the first point measured along the (2) laterally 13. The microporous membrane according to claim 11 or 12, wherein the distance between the final points is at least 90% of W, or (3) the puncture strength is 4,500 mN / 20 μm or more. (1) at least one of the number of the points is at least 40, the standard deviation of air permeability value does not exceed 15 seconds / 100 cm ^3/20 [mu] m, and the first point measured along the (2) laterally 12. The microporous membrane according to claim 11, wherein the distance between the last points is at least 95% of W, or (3) the puncture strength is 4,500 mN / 20 μm or more. A battery separator comprising the microporous membrane according to claim 11 or 12. A battery comprising an electrolyte, an anode, a cathode, and the battery separator of claim 19. 21. The battery is a lithium ion secondary battery, a lithium-polymer secondary battery, a nickel-hydrogen secondary battery, a nickel-cadmium secondary battery, a nickel-zinc secondary battery, or a silver-zinc secondary battery. Battery. The battery of claim 21, wherein the cathode has a cathode active material layer on the current collector and a current collector capable of absorbing and discharging lithium ions. 22. An electrical circuit comprising the battery and linear circuit element and / or nonlinear circuit element of claim 21, wherein the battery acts as a source or sink of charge for the linear and / or nonlinear circuit element. .